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Published by Maney Publishing (c) IOM Communications Ltd Effects of hydrostatic pressure on mechanical behaviour and deformation processing of materials J.J. Lewandowski and P. Lowhaphandu The processing and subsequent mechanical behaviour of a variety of commercially important materials are affected by the imposed stress state. In this review, the experimentally documented effects of superimposed pressure on deformation under quasistatic conditions are summarised, followed by a presentation of the effects of superimposed pressure on the fracture behaviour of a variety of materials including both ductile and brittle systems. It is shown that the pressure responses of a variety of materials show distinct differences and the potential reasons for these differences are presented. Finally, in the light of all of these observations, the effects of changes in stress state on deformation processing are reviewed. In particular, the evolution of hydrostatic stresses during various forming operations is covered followed by a review of published work and the potential benefits of superimposing pressure during processing of a variety of materials. IMR/328 © 1998 The Institute of Materials and ASM International. The authors are Professor and Research Assistant, respect- ively, in the Department of Materials Science and Engineering, The Case School of Engineering, Case Western Reserve University, Cleveland, OH 41106, USA. List of symbols a minimum specimen radius G m shear modulus of matrix k linear compressibility k a linear compressibility in a direction k c linear compressibility in c direction k r linear compressibility in any direction k y macroscopic shear yield stress K material constant K Ic fracture toughness 11K stress intensity range K m bulk modulus of matrix K p bulk modulus of particle n work hardening exponent P applied or superimposed hydrostatic pressure P ex extrusion pressure r reduction r n distance from centre of specimen along plane of neck r p particle radius R radius of curvature at neck or notch Rex extrusion ratio sij elastic compliance Vf volume fraction of microvoids a extrusion die angle r direction cosine E[ fracture strain G n critical strain for microvoid nucleation f.l coefficient of friction (J true tensile stress (J B yield strength of billet material (Jc critical interfacial cohesive strength of interface (J[ brittle fracture stress in tension (J flow flow stress (Jm mean normal stress (Jm,eff effective mean normal stress (In critical mean stress required to initiate plastic flow or internal necking in intervoid matrix (JT hydrostatic tension (J y uniaxial yield strength in tension if effective stress (J 1, (J 2, (J 3 principal stresses t max maximum shear stress Introduction Over past decades, extensive studies have been con- ducted by a variety of researchers on the effects of superimposed hydrostatic pressure on the deforma- tion and fracture behaviour of materials tested under quasistatic conditions, including related topics such as hydrostatic extrusion. 1 - 312 The pioneering work conducted by Bridgman 2 - 44 documented the effects of superimposed hydrostatic pressure (at levels up to 3 GPa) on a variety of properties, including the flow and fracture behaviour (e.g. ductility) of a variety of monolithic metals. Subsequent experimental work by a variety of researchers focused on the source(s) of the improved ductility.45-201 Concurrent with these experimental investigations was the development of a number of theoretical models focusing on addressing/predicting the effects of changes in stress state on the deformation and fracture of metals,80,82,96,116,117,136,151,313,314 metallic compos- ites,315-320metallic glasses,321-324 and geologic mater- ials. 267 Bridgman's work 2 - 44 and other more recent work, also investigated the effects of superimposed pressure on the mechanical behaviour of non- metallic materials, including intermetallics,154-170 cer- amics,171-181 composites,182-201 and polymeric202-235 based systems. There is also an extensive body of literature236-28o on the effects of superimposed press- ure on geologic materials. In many of the materials systems studied, significant pressure induced changes to the flow stress and ductility have been observed. Such observations may have important implications on their service perform- ance, as the stress state encountered in the service of many structural materials is often not uniaxial. This is clearly true in various applications where pressure is present, whether it is in a pressure vessel; at significant depths in the ocean or the earth; in the vicinity of a shock wave propagating through a solid;325 or due to the triaxial stresses developed International Materials Reviews 1998 Vol. 43 No.4 145
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Effects of Hydro Static Pressure on Mechanical

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Page 1: Effects of Hydro Static Pressure on Mechanical

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Effects of hydrostatic pressure on mechanicalbehaviour and deformation processing of materialsJJ Lewandowski and P Lowhaphandu

The processing and subsequent mechanicalbehaviour of a variety of commercially importantmaterials are affected by the imposed stress stateIn this review the experimentally documentedeffects of superimposed pressure on deformationunder quasistatic conditions are summarisedfollowed by a presentation of the effects ofsuperimposed pressure on the fracture behaviourof a variety of materials including both ductile andbrittle systems It is shown that the pressureresponses of a variety of materials show distinctdifferences and the potential reasons for thesedifferences are presented Finally in the light of allof these observations the effects of changes instress state on deformation processing arereviewed In particular the evolution of hydrostaticstresses during various forming operations iscovered followed by a review of published workand the potential benefits of superimposingpressure during processing of a variety ofmaterials IMR328

copy 1998 The Institute of Materials and ASM InternationalThe authors are Professor and Research Assistant respect-ively in the Department of Materials Science andEngineering The Case School of Engineering CaseWestern Reserve University Cleveland OH 41106 USA

List of symbolsa minimum specimen radius

Gm shear modulus of matrixk linear compressibility

ka linear compressibility in a directionkc linear compressibility in c directionkr linear compressibility in any directionky macroscopic shear yield stressK material constant

KIc fracture toughness11K stress intensity rangeKm bulk modulus of matrixKp bulk modulus of particle

n work hardening exponentP applied or superimposed hydrostatic

pressurePex extrusion pressure

r reductionrn distance from centre of specimen along

plane of neckrp particle radiusR radius of curvature at neck or notch

Rex extrusion ratiosij elastic complianceVf volume fraction of microvoidsa extrusion die angler direction cosineE[ fracture strain

Gn critical strain for microvoid nucleation

fl coefficient of friction(J true tensile stress

(J B yield strength of billet material(Jc critical interfacial cohesive strength of

interface(J[ brittle fracture stress in tension

(J flow flow stress(Jm mean normal stress

(Jmeff effective mean normal stress(In critical mean stress required to initiate

plastic flow or internal necking inintervoid matrix

(JT hydrostatic tension(J y uniaxial yield strength in tensionif effective stress

(J 1 (J 2 (J3 principal stressestmax maximum shear stress

IntroductionOver past decades extensive studies have been con-ducted by a variety of researchers on the effects ofsuperimposed hydrostatic pressure on the deforma-tion and fracture behaviour of materials tested underquasistatic conditions including related topics suchas hydrostatic extrusion1-312 The pioneering workconducted by Bridgman2-44 documented the effectsof superimposed hydrostatic pressure (at levels up to3 GPa) on a variety of properties including the flowand fracture behaviour (eg ductility) of a variety ofmonolithic metals Subsequent experimental work bya variety of researchers focused on the source(s) ofthe improved ductility45-201 Concurrent with theseexperimental investigations was the developmentof a number of theoretical models focusing onaddressingpredicting the effects of changes instress state on the deformation and fracture ofmetals808296116117136151313314metallic compos-ites315-320metallic glasses321-324 and geologic mater-ials267 Bridgmans work2-44 and other more recentwork also investigated the effects of superimposedpressure on the mechanical behaviour of non-metallic materials including intermetallics154-170 cer-amics171-181 composites182-201 and polymeric202-235based systems There is also an extensive body ofliterature236-28o on the effects of superimposed press-ure on geologic materials

In many of the materials systems studied significantpressure induced changes to the flow stress andductility have been observed Such observations mayhave important implications on their service perform-ance as the stress state encountered in the service ofmany structural materials is often not uniaxial Thisis clearly true in various applications where pressureis present whether it is in a pressure vessel atsignificant depths in the ocean or the earth in thevicinity of a shock wave propagating through asolid325 or due to the triaxial stresses developed

International Materials Reviews 1998 Vol 43 No4 145

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146 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

from differences in the thermal expansion coefficientbetween the matrix and the reinforcement in a com-posite In addition to providing experimental inputto various modelling efforts focusing on the funda-mentals of flow and fracture such information is alsorelevant to the formability of a material In this casethe broadest definition of formability relates to theability of the material to sustainaccommodate plasticflow often to very high levels of strain This caninclude such operations as rolling forging extrusionsheet metal forming etc While the formability deformability depends on a combination of factorsincluding the chemical composition microstructuretemperature and deformation velocity critical para-meters include the stress state and the superpositionof any residual stresses Since the stress state experi-mentally obtained where testing is conducted withsuperimposed hydrostatic pressure is closely relatedto that achieved (or desired) in many of the form-ing operations described above the data obtained(eg flow stress ductility etc) from such testing arevery relevant to the formability In addition many ofthe models for deformation processing require asinput the flow stress at very high values of strain Astesting with superimposed pressure typically increasesthe strain to fracture of many industrially importantmaterials to levels well beyond that obtained inuniaxial tension such large strain data can also beused as input for the various modelling efforts aimedat the forming operations described above

This review summarises the published experimentalobservations of the effects of superimposed hydro-static pressure on the mechanical behaviour obtainedunder quasistatic conditions for a variety of inorganicmaterials including recently obtained data on inter-metallics and metallic composites Although there isa body of similar literature on organic materials andceramic based systems this is beyond the scope ofthe present review However some relevant referenceshave been provided for the behaviour of organicmaterials202-235 which exhibit highly pressure sensitivebehaviour as well as for ceramic and geologic mater-ialsl71-181236-280tested with superimposed pressureThis review is divided into separate summaries andbegins with the testing techniques typically utilised instudies where quasi static loading conditions aredesired The effects of superimposed pressure on theflow fracture and deformation processing of a varietyof inorganic materials including intermetallics andcomposites follows The data summaries were pre-pared from published work on the various systemslisted while references to the original published worksare provided in the text as well as in each of theindividual data summaries The primary factors con-trolling flow and fracture will precede the presentationof the data summaries while the data summariesconclude with a short discussion of the major obser-vations Details of the various observations and issuesmay be found in the references cited

Experimental test techniques utilisedin high pressure testingHigh pressure mechanical testing13336 of struc-tural materials under quasistatic conditions has

International Materials Reviews 1998 Vol 43 NO4

Top plunger

Pressure gauge

Load cell

Specimen

Window

Support

Extension rod

High pressurecontainer

Bottom plunger

25mm

Schematic diagram of oil based high pressuredeformation apparatus3672 122 126269326-329

been conducted using a variety of high pressuremedia including solid171-174179249251273277326327liquids36122126269326-329and gases271273330The lasttwo groups are typically preferred as non-hydrostaticconditions may exist with solid media Typical liquidmedia include a variety of oils as well as kerosenepentane and naphtha while gas media include inertgases (eg Ar He) and hydrogen Pressure levels inexcess of 3 GPa have been obtained with such sys-tems High pressure tests well in excess of 3 GPa havebeen conducted using diamond anvil cells326327331and other test systems where the volume of materialtested in such studies is typically too small to sampleenough of the material to be of use to the structuralmaterials community where size effects on materialproperties have been observed Significantly higherpressure (eg gt 10 GPa) may be present in variousshock loading experiments conducted under impactor high velocity experiments as reviewed elsewhere325and not covered in this review The liquid mediasystems utilised in quasistatic testing are typicallylimited to use below 300degC because of the potentialdecompositioncracking of the oil while the solid-and gas-based systems have been utilised at gt 1000degCThis review focuses primarily on data obtained oneither oil- or gas-based systems and those opera-ted at relatively modest (eg lt 300degC) temperaturesthough references to tests conducted at high pressureand high temperature are provided (Refs 171-181236-244 246 247 251-253 255 258 260-262 264

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 147

pressure vessel mantle

7y 6_10_m_m f-pressure vessel liner

servohydraulicactuator bull

argon gas line

a internal load cellb specimen

2 Schematic diagram of gas based high pressure deformation apparatus271273330334

265 268 269 271-273 276-278) References to theeffects of superimposed pressure on creep265281-286have also been provided though this aspect is notcovered in this review

Pressure generation in the oil based systems ofteninvolves compression of the fluid in a pressure vesselvia pressing a plunger in to the bore of a pressurevessel as shown in Fig 1 Pressure is typically moni-tored via the use of a manganin coil pressure gaugethat is exposed to the high pressure environmentManganin coils are used in this case because of thehighly reproducible and linear manner with whichthe resistance of the coil varies with changes inpressure22332 Simple pressurisation experiments canbe conducted with such systems whereby a materialis placed into the pressure vessel and the fluid (ieoil) is compressed to produce a measurable level ofhydrostatic pressure In such simple pressurisationstudies the pressure is subsequently reducedremovedin order to measure the resulting behaviour of thematerial at atmospheric pressure Typically both thepressurisation rate and depressurisation rate aremonitored and kept at a constant low value becauseof the possibility of significant specimen heating (orcooling) during the pressurisation (depressurisation)cycles

Mechanical testing with superimposed hydrostaticpressure has also been conducted on similar devicesto that shown in Fig 1 In these cases the specimenis typically inserted into the load train assemblypresent in the pressure vessel shown in Fig 1 followedby pressurisation of the fluid and the subsequenttension (or compression) testing of the specimen atthe desired level of superimposed hydrostatic pressureIn such tests the high pressure fluid has access to allsurfaces of the specimen It is important to monitorcontinuously (and keep constant) the pressure dur-ing the test in addition to having the capabilityto monitor accurately the load and displacementrequired to deform the specimen under pressure aspointed out elsewhere33o In oil based pressure systemssuch as that shown in Fig 1 the confining (iehydrostatic) pressure is kept constant via either using

an intensifier or retracting the bottom hydraulicpiston while inserting the top plunger In such testingthe use of external load cells (ie positioned on theload train but outside of the pressure vessel) mayproduce erroneous data for the load required todeform the specimen because of the variable amountof seal friction which results during the generation ofpressure in the chamber In an attempt to determinethe load on the specimen inside the vessel moreaccurately pressure compensated load cells consistingof a measuring load cell and a compensating loadcell were developed330333 as shown schematicallyin Fig 1 Displacement andor strain measurementin such studies has typically relied on monitor-ing piston displacement though more recentstudies103 155-157161-163189190192-195197have utilisedpressure compensated strain gauges affixed to thespecimen surfaces In some studies195197213the press-ure vessel was fitted with machined cross-bores andtransparent quartz windows as shown in Fig 1 whichenabled in situ monitoring of deformation and thedevelopment of necks under pressure

Gas based systems like that shown schematicallyin Fig 2 typically utilise a pressure intensifier togenerate pressure that is contained within a multi-walled pressure vessel where the volume of gas pre-sent at high pressure in the vessel is kept as low aspossible because of the danger associated with thestored energy Such systems often utilise many of thesame types of diagnostic techniques as that describedabove though direct visual monitoring of the speci-men during deformation has not been conductedbecause of the inherently higher danger associatedwith gas based systems Pressure fluctuations duringmechanical testing in gas based systems are typicallymuch less than those of the oil based systems wherethe pressure generation techniquedevice is directlylinked to the piston which controls displacement ofthe specimen

Tables 1 and 2 summarise many of the variousinvestigators that have utilised high pressure testingto evaluate the mechanical behaviour of materialsTable 1 summarises the maximum pressure utilised

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 149

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150 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Table 2 Summary of investigations on effects of hydrostatic pressure on mechanical behaviour ofinorganic materials - categorised by class of material

Pressu re range

Materials Researcher(s) Failure mode P MPa Measured properties Note

0-27 (UTS) Ef

Ef

Ef

0-15 (UTS) Ef void fraction0-19 (UTS) Ef void fraction

PrepressurisedprestrainedTemperature upto 600aC

Prepressurised

Prepressurisedprestrained

Interrupted testInterrupted test

Prepressurised

Prepressu rised

Prepressu rised

PrestrainedPrepressurised

Interrupted test

Prepressu rised

ay af poundf

ay

ay af EI

ay UTS 8f

Ef

(Iy af poundf

ay af EI

Ef

ay Ef EI n K1c

EI

Ef

Ef

qEf

dadn versus ~Kaf Ef

ay UTS Ef

(Iy UTS qay Ef

(Iy Ef voids quantification

ay af Ef

Ef

ay UTS nEf voids quantification(Iy af qay

ay

dadn versus ~Kay UTS Ef

ay

ay

ay (If Ef

ay UTS Ef

ay UTS Ef

Ef

ay EIEf

ay Ef

Ef

J

CRSS

0-58

0-12

0-270-12

0-7S

0-26

030-110-08

0-330-170-200-08

0-120-110-1S01-020-070-36

OS

0-103

01-500

01-3060

01-290001-S0001-140001-50002000

01-250001-31001000

01-600

01-6900-48001-60001-600

01-20001-296001-35001-80001-900

01-300

01-60001-52001-30001-62001-3501-92001-69001-69001-300

01-110001-60001-7

01-110001-S0001-69001-345100001-2250

01-70001-90001-345150001-69050017201-210001-126001-110017201-110001-110001-3501-69001-110001-110017201-69001-970

Cleavage

Cleavage

MVCshear

MVCshear

MVCshearMVCshear

ShearMVC

Intergranular

MVC

MVCshearMVCshear

MVCshear

MVCdelamMVCshear

MVCshear

MVCshear

MVCshear

Nishihara et al114

French and Weinrich89

Pugh and Green 123

Vajima et al149

Pugh and Green 123

Plumbridge et af121

HU93

ZOk152

ZOk152

Lewandowski etal189190

Liu andLewa ndowski103 195

Korbel et al99

Auger and Francois5051

Franklin et al84

Bridgman36

Ball et al53

Bullen et al64

Mellor and Wronski108

French andWeinrich88141

Vajima et al149

Pugh and Green 123

French and Weinrich85

Weinrich andFrench85141

Omura119

Bridgman36

ZOk152

Vajima et al149

Vajima et al149

Bridgman36

Dobromyslov et af79

Galli and Gibbs90

Kuvaldin et af100

Mellor and Wronski108

Spitzig 135

Vajima and Ishii147148

Vajima et al149

Ohmori et al118

Bullen et al65

Davidson andAnsell7576

Vajima et af149

Itoh et al95

Ohmori et al118

Worthington 144

Pugh and Green 123

Wagner et al140

Johnson et al97

Davidson et af74

McCann et al106

Brownrigg et al63

Johnson et af97

Spitzig et al133

Spitzig et al133

Plumbridge et al121

ZOk152

Spitzig et al134

Spitzig et al134

Johnson et al97

Zok and Embury152153

ZOk152

MoMoMoMoMo

7075AI-T47075AI-T6517075AI

Cu alloysPure

PureERCH CuLeaded brassa-brass a-fJ brass

70-30 40-60 brassy-brassCu-002BiCu-(15-40)ZnCu-(45-97)Ge

Ni alloyPure

bcc metalsCrCrCr

Mo

Fe-(O02-049)CMild steel (OOSC)Mild steel (O14C)Fe-3SiCast ironsSpheroidised cast iron101S steel1045 steel1045 steel1045 steel (spheroidised)4130 steel4310 steel4330 steel4360 steel4340 steelMaraging steelHV SO steelHV 130170180 steels01 tool steelTi-V steel

AI alloysPurePurePureAI-1 Si-07Mg-04MnAI-Cu-Mg-Si61S AI-T42014AI-T6AE2124AI-UAOAMB85-UAOA

6061AI-UAOA

Metals

Ferrous alloysSingle crystal FePure FePure FePure FeArmco FeFe-(0004-11)C

Mo Robbins andWronski131132

Cleavage 01-500

CRSS critical resolved shear stress delam delamination dadn crack propagation rate EI elongation HV Vickers hardness J J-integral MVC microvoidcoalescence UTS ultimate tensile strength

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 151

Table 2 (cant)

Pressure range

Materials Researcher(s) Failure mode P MPa Pj(fy Measured properties Note

Metalsbee metalsNb Bridgman36 01-2850 (ff qTa Bridgman36 01-2850 (ff [f

Ta Nishihara et al114 01-500 ayUTS rof Temperature upto 600C

Ta Robbins and Wronski131 1500 (fy Prepressu rised0-500

W Bridgman36 01-2840 af lofW Das and Radcliffe73 01-1100 0-15 (ff af lofW Daga71 01-1100 0-20 ay (ff qW Davidson et al74 CleavageMVCjshear 01-1600 qW Mellor and Wronski108 2800 (fy af EI Prepressu rised

prestrainedhcp metalsBe (PM) Aladag45 Intergranularj 01-980 af [f

Aldag et al46 transgranularBe (PM) Andrews and 01-2700 Prepressurised

Radcliffe49Be (ingot) Aladag45 Transgranular 01-980 0-38 (fy af [f

Aldag et al46

Be (castrolled) Bedere et al55 Intergranularj 01-1500 0-122 (ly af [f

transgranular shearCd Nakajima et al111 01-600 ayCo Davidson et al74 CleavagejMVCjshear 01-2350 f~Mg Davidson et aJ74 MVCjshear 01-1800 4Mg Pugh and Green 123 01-460 [fAZ91 (PM) Lahaie et al101 Intergranularshear 01-690 0-22 (fy ltofAZ91-T4jT6 Lewandowski et al193 01-380 af (f

Zn Davidson et al74 Brittlejplastic rupture qZn Pugh and Green 123 Cleavageplastic 01-138 ay q

ruptureZn-41AI Pugh and Green 123 01-410 ltofTi-7 AI-2Nb-1Ta (x) Johnson et al97 172 02 ay af lt1 Prepressu risedTi-6AI-4V (ajm Johnson et al97 172 02 (fy (ff Gf Prepressu risedTi-13V-l1 Cr-3AI (x) Johnson et al97 172 0middot2 ay af q Prepressurised

Metal matrix composites

AI matrix2014-20SiCp-T6jAE ZOk152 MVCshear 01-980 0-24 ay UTS Gf

2124-14SiCw-UAjOA ZOk152 MVCshear 01-690 0-20 ay UTS l12014-20SiCp-T6jAE Mahon et al198 MVCjshear 01-980 0-24 ay UTS l12124-14SiCw-UAjOA Vasudevan et al201 MVCjshear 01-690 0-20 ay UTS [f

MB85-15SiCp-UAjOA Lewandowski MVC 01-300 0-08 (ly af (fet al189190

M B85-15SiCp-UAjOA Liu 195 MVC 01-300 0-08 ay (ff q6061AI-15AI203-UAjOA Liu et al194195197 MVC 01-300 0-11 ay af q Damage

quantification6090AI-25AI203-SAjT6 Lewandowski et al193 MVC 01-400 GfMB78-15SiCp-UAjOA Singh and MVC 01-500 q Damage

Lewandowski199 quantificationA356-1 Oj20SiCp- T6 Embury et al184 MVC 01-850 q Damage

quantificationAI-AI3Ni Zok 152 MVC 01-690 0-45 ay UTS lt1

Mg matrixAZ91-20SiCp-T4 Lewandowski et al193 01-350 0-12 GfAZ91-19SiCp15 llm-T6 Lewandowski et al193 MVC 01-440 0-14 ay UTS af [f Damage

quantificationAZ91-20SiCp52 llm-T6 Lewandowski et al193 MVC 01-490 0-19 ay UTS af [f Damage

quantificationCu matrixCu-28W Zok152 MVC 01-690 UTSq

IntermetallicsNiAI Margevicius and Transgranularj 01-1400 0-140 (ly (ff Gf wj

Lewandowski155161163 inte rg ra nul ar PrepressurisedNiAI Weaver et al166167 Prepressu risedNi3AI Zok et al152170 Intergranular 01-965 af GfAI3Ti Witczak and Varin 169 2000 ay af lof HV PrepressurisedAmorphous metalsPd Cu Si Davis and Kavesh323 Shear 01-690 0-047 af EfZr Ti Ni Cu Be Lewandowski et al324 Shear 01-650 0-035 af Ff

CeramicsAI203 Bridgman36 2350-2960 afB203 Bridgman3637 2350-2960 af Gf density changeLiF Hanafee and 01-1300 Dislocation velocity

Radcliffe 176MgO Weaver and Brittlejshear 01-1000 ay af Ff

Paterson 180181NaCI Bridgman36 2350-2960 af [f

CRSS critical resolved shear stress delam delamination dajdn crack propagation rate EI elongation HV Vickers hardness J J-integral MVC microvoidcoalescence UTS ultimate tensile strength

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152 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

and any pressure variation reported during the testin addition to the load and strain measurementtechniques reported by the various investigators onthe materials listed Table 2 provides a similar list ofinvestigations organised by the type of material (egmetal intermetallic composite) tested as well as bythe crystal structure (eg bcc fcc hcp) of the metalsunder investigation Included in Table 2 are thespecific properties measured by each of the investi-gators and any comments related to the failure modespresent References to the works in Tables 1 and 2are provided while the specific data summariesappear in subsequent figures In most of the studieswhere testing is conducted with superimposed hydro-static pressure the specimens have been coated orjacketed274 with some impervious membrane (egpolymer Cu shrink fit tubing etc) in order to preventingress of the pressure medium into any surfacecracks porosity etc274 The membrane utilised istypically very thin and does not contribute signifi-cantly to the load bearing area of the specimenFurthermore pressurisation of specimens shieldedwith such membranes in and of itself has not pro-duced changes to the subsequent flow stress obtainedat atmospheric pressure

1

-2-1

o~ 1cr

2

3 Yield surface plotted in principal stress spacefor fully dense isotropic and homogeneousmaterial335336

(2)

(4)

(5)

ka = 511 + 512 + S13

kc = 2S13 + 533

shear stresses developed owing to the differences incompressibility between the matrix and the secondphase128 The maximum shear stress [max at thematrixsecond phase interface has been separatelyestimated by Das and Radcliffe73 and Ashby et al337

for a spherical particle and is given by

3Gm ( Km -Kp )[max = K 3K + 4G pm p m

where Gm is the shear modulus of the matrix Km

and K the bulk moduli of the matrix and the sec-ond phase respectively and P the applied hydro-static pressure Dislocations are generated when[max reaches the nucleation stress for dislocationgeneration which can be theoretically predicted ordetermined experimen tally338

Another manner in which shear stresses are gener-ated in polycrystalline materials through the simpleapplication of hydrostatic pressure is through theanisotropy of elastic constants91128 Crystals of allsystems except the cubic system can change shapewhen subjected to hydrostatic pressure cubic crystalshave isotropic bulk moduli The volume compress-ibility which is the inverse of the bulk modulus isthe pressure induced change in volume of a crystalnormalised to its original volume and the linearcompressibility k is the amount of pressure inducedlength change in a straight line normalised to itsoriginal length For the cubic system k is independentof orientation and is related to the elastic compliance5ij through

k = 511 + S12 bull bull bullbull bull (3)For the trigonal hexagonal and tetragonal systemstwo constants are required the value in the a directionka and the value in the c direction kc These compress-ibilities are related to the elastic compliance 5ij by

Effects of superimposed pressure onstress state in cylindrical specimensConditions present before necking incylindrical specimensPlastic deformation in metallic systems tested at lowhomologous temperatures primarily occurs via dislo-cation generation andor movement via shear stressesoften referred to as conservative motion or glidePlastic deformation under such conditions occurswhen the effective stress (j equals the yield strengthin tension (Jy where the effective stress is given as

- 1 ( )2 ( )2 ( )2] 120=0[(J1-(J2 + 02-(J3 + (J3-(J1

(1)and (Jb (J2 and (J3 represent the principal stressesThe application of a purely hydrostatic stress (ie(J1 = 02 = (J3) produces no shear stress in a homo-geneous and isotropic material as shown by the 3-Dyield surface plotted in stress space in Fig 3 Ahydrostatic stress is represented as the axis of thecylinder in Fig 3 and since such stresses never touchthe yield surface there should be no effect ofpressurisationpressure soaking on the subsequentflow behaviour when uniaxial testing is conducted atatmospheric pressure Pressurisation in this casedenotes the simple application of hydrostatic pressureto a material and its subsequent removal Thereshould similarly be little effect of superimposed press-ure on yielding when testing is conducted on acylindrical specimen in the presence of a confining(ie hydrostatic) pressure as the stress state up to theultimate tensile stress (UTS) (ie before necking) insuch specimens consists of the uniaxial stress plusany superimposed hydrostatic pressure

However simple pressurisation can serve as ameans for generating dislocations in a materialaround inclusions and other defects as there are local

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 153

1

4 Yield surface plotted in principal stress spacefor material containing void fraction of a 0057and b 0180 (Ref 336)

1

1

a~l 05cr

o~ta

-05

-1

-1

(a)

(b)

The linear compressibility in any other direction kris given by

kr = ka + (ke - ka)r2 (6)

where r is the direction cosine with subject to thec axis

If non-cubic metals can change shape because ofpressurisation then a random aggregate of manycrystals when subjected to unit hydrostatic pressurewill develop shear stresses across grain boundaries Itis this shear stress which produces dislocation gener-ation in anisotropic materials

The degree of anisotropy in these non-cubic systemsis given in terms of the ratio keka The anisotropy ofa number of hexagonal metals is given in Table 3Those metals with a high degree of anisotropy Cdand Zn have been shown91339 to require only modestlevels of pressure ( 300 MPa) to induce plastic strainin the grains while metals with ratios close to one(where a cubic metal equals 10) Zr and Mg requiredthe highest pressures ( 2middot6 GPa) to produce onlytrace amounts of plastic deformation Although TEManalyses have confirmed the presence of pressureinduced dislocations around inclusions in less pureFe and Fe-C alloys containing inclusions65139 highpurity cubic metals such as Cu AI Fe and Ni haveshown no such plastic deformation after pressuris-ation to levels up to 1 GPa (Refs 109 339)

Porous materials consisting of either interconnectedor isolated pores are also highly pressure sensitive340provided the pressure medium is shielded from thespecimen to prevent ingress of the pressure medium(ie gas liquid) into the pores The 3-D yield loci forsuch materials are distinctly different from that shownin Fig 3 for homogeneous and isotropic materialsShown in Fig 4 are 3-D yield loci for porous materialscontaining increasing levels of porosity335336341342It is clear that the application of a hydrostatic pressureof sufficient magnitude in these cases can touch theyield surface and thereby produce plastic flowExamples of such effects are provided in works onporous Fe (Refs 62 137)

where Oflow is the flow stress a the minimum specimenradius R the radius of curvature at the neck or notchand rn the distance from the centre along the planeof the neck

Since the notchneck geometry will often changewith additional deformation the level of triaxialtensile stress resulting from deformation of such

International Materials Reviews 1998 Vol 43 NO4

mens) when subsequently tested in tension also experi-ence triaxial tensile stresses in the neckednotchedregion In this case the major difference between thenecked region which evolved during deformation andthat simulated by prenotching a pristine (ie non-deformed) specimen relates to the differences indeformation history (and any damage) present in thenecked region as compared to the notched regionBridgman provided an estimate of the additionalhydrostatic tension OT in the plane of a neck ornotch2436 as

Conditions present past necking incylindrical specimensOnce a neck begins to form in a cylindrical tensilespecimen tested at atmospheric pressure triaxialtensile stresses develop in the necked region Boththe magnitude and location of such triaxial stressesvary with location in the neck which develops withadditional deformation Prenecked (eg notched speci-

Table 3 Linear compressibility and anisotropyfactors for some non-cubic materials(Refs 128 339)

Lattice ratioLinear compressibility MPa

Metal cia c axis ke a axis ka Ratio keka

Cadmium 18856 1890 x 106 217 X 106 870Zinc 18564 1341 x 106 201 X 106 670Bismuth 26095 1645 x 106 684 X 106 240Magnesium 16235 1016 x 106 1016 X 106 1middot00Zirconium 1middot5931 380 x 106 3middot80 X 106 1middot00Titanium 15870 270 x 106 270 X 106 100Beryllium 15684 227 x 106 291 X 106 078

(a 12 )

OT = Oflow In 1 + 2R - 2a~ (7)

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154 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Superimposed Hydrostatic Pressure MPa

4340 tenlpered 3000C 152

4340 tempered (eQ 5000C 152

4340 tempered 7000C 152

o 4310-Lower Yield 133

bullbull 4330-Lower Yield 113

6 01 Tool Steel Hard 152

6 01 Tool Steel Mediunl 152

6 01 Tool Steel Soft 152

[S ri-V Steel 9500C FRT 152

fpound Ti-V Steel 700degC FRT 15~

bull 7075AI-T651(TR) 5051

bull 7075AI-T65 I(WR) 5051

T 7075AI-T65I (RW) 5051

() 201411 1(21)

EE BY -80 1ower Yield 134

bull Maraging-Unaged (Ten) 134

bull Maraging-Unaged (Comp) ]34

bull Maraging-Aged (Ten) 134

bull1200

(a)

bullbull

1000

EB

[SJ

800600400200

bull bull bull bullbullbullII bullbull JI bullbull Q bullbull bull

~ 6III II II bull

j 6 i i6

o

20

o

=~~ 15Q)~~

rJ)

0

~ 10~

e~ 05Z

~~ 1500

2000

=~eJ)

~ 1000~~

rJ)

e-Q)

~

00(b)

(gt 2124J() () I

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure

5 Effect of pressure on yield strength of various bee and fcc metallic alloys

specimens will vary past necking in the cylindricalspecimen Thus while the level of superimposedhydrostatic pressure has been kept relatively constantin many of the studies listed in Tables 1 and 2 thetriaxial stresses present in the neck during tests withsuperimposed pressure will depend on a variety offactors including the neck geometry level of superim-posed pressure and the flow stress of the materialIt is important to note that some studies investigat-ing the effects of superimposed pressure on tensiontests have been conducted under conditions suchthat compressive triaxial stresses were present in thenecked region In these cases the levels of superim-posed pressure were high enough to overcome thetriaxial tensile stresses which developed in the evolv-ing neck Thus the ability to monitor visually thedevelopment of the neck during tests with superim-posed pressure as described above or conductinginterrupted tests where the neck can be physicallymeasured outside of the high pressure environmenthas some merits858689103197213

Effects of superimposed pressure onflow behaviourEffects of superimposed pressure onyield stressFigures 5-8 summarise published data on the effectsof pressurisationpressure soaking as well as tensiletesting at different levels of superimposed hydrostaticpressure on the yield strength typically reported asthe 0middot2 offset yield strength In the former tests theyield strength was measured at atmospheric pressureafter pressurisation while the measurements of yieldstress in the latter cases occurred during tensile testsconducted with superimposed hydrostatic pressureThe pressure medium utilised in the studies summar-ised was either an oil medium or Ar gas and wasconfirmed to be hydrostatic Figure 5 summarisesdata obtained on a variety of steels and aluminiumalloys while Fig 6 shows similar data obtained on avariety of single phase metals possessing a bcc crystalstructure Figure 7 is a plot of the same type of

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 155

___bull __ Ar111co Iron 65

5b 6b 7b and 8b are plots of the ratio of the yieldstrength obtained at pressure (or after pressure soak-ing) to that of the control material (ie no pressuresoaking) in the manner utilised by a number ofinvestigators henceforth this is called the normalisedyield strength Pressure independent yielding is rep-resented by the horizontal line at 1middot0 for the normal-ised yield strength in Figs 5b-8b It is clear fromFig 5a that a number of conventional structuralmetallic alloys exhibit nominally pressure independ-ent yielding behaviour as predicted by equation (1)Slight positive deviations for monolithic materials (ienormalised yield strengthgt 1 in Fig 5b) have beenexplained as in part due to the pressure depend-ence of the shear modulus which though modestis non-zero for various metallic materials136Models313314 have been developed to predict suchpressure dependent yielding in metallic materials andmetallic glasses321-323 and a few studies have invokedsuch models to explain such pressure dependence ofthe yield stress136 It should be noted that there havebeen observations of materials which exhibit muchgreater positive deviations than those of the monolithicmetals summarised in Fig 5a and b For example ithas been clearly shown that superimposed pressuresignificantly inhibits dislocation mobility in LiFthereby elevating the flow stress above that obtainedat atmospheric pressure176

It is also clear that some of the monolithic metalsshown in Fig 5a and b as well as a variety of bccmetals (cf Fig 6a and b) and certain chemistries ofthe intermetallic NiAI shown in Fig7a and b ex-hibit a significant decrease in the yield strength afterpressure soaking or during tests conducted withsuperimposed pressure In these cases the materialstypically exhibited a yield point and Liiders exten-sion before pressure soaking or testing with superim-posed pressure Pressurisation (andor testing withpressure) was shown to remove the yield pointand Liiders strain and thereby reduce the yieldstrength155157159161162166167as illustrated for castextruded NiAI in Fig 7c As shown in Figs 6a andband 7a and b large reductions in yield strengthwere obtained in Fe (Refs 65 147) Cr (Refs 59 6466 72) and commercially pure NiAI (Refs 155 157161-163) that had been cast and extruded ExtensiveTEM analyses in these cases revealed that pressureinduced dislocation generation occurred at non-metallic inclusions and other inhomogeneities in thesematerials6465155157158161an example of which isshown in Fig 7d (Ref 157) The generation of thesemobile pressure induced dislocations thereby reducedthe yield strength while subsequent thermal agingstudies conducted for sufficient time-temperaturecombinations at atmospheric pressure enabled relock-ing of the dislocations by interstitial impurities (egC) and a return of the yield point and Liidersstrain6465107147166as illustrated for NiAI in Fig7c(Ref 159) Similar studies166167 conducted on highpurity NiAI failed to reveal a yield point and anysubsequent effect of pressurisation on the yield stressas shown in Fig 7a and b consistent with sucharguments Pressurisation of the largest grained Fein Fig 6a and b (Ref 147) to increasingly higherpressures eventually produced excessive generation

International Materials Reviews 1998 Vol 43 NO4

1200

(a)

(b)

---)

1000800600

~_-----1-~ - --

400200

- - Chromium 64

bull - Iodide Chromium 72

Superimposed Hydrostatic Pressure MPa

bull ~ ~- Y- -y_~~~ - - -9

-------

cOil 15cQJ

000 10~~5 050Z

000

800

eo 700~~ 600pound 500eiJcCJ 400V)

0 300~~ 200

100o

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

20

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

6 Effeet of pressure on yield strength of variousbee metals GS grain size

--0 Fc GS=11Jlnl 147

-0 Fe GS=14Jlm 147

-[S- Fe GS=19Jlm 147

-83- - Fe GS=30Jlm 147

-- - Fe GS=450~lIn 147

6 - - PM T 72- ungsten

-pound --Arc-Melted Tunsten 72

information for the intermetallic NiAI which possessesa B2 (ie bcc derivative) crystal structure while Fig 8is a plot of data from more recent work on compositesbased on either aluminium or magnesium alloymatrixes The data reported for the control materials(ie no pressure soaking) occur on the ordinate at0middot1 MPa (ie atmospheric pressure) Figures 5a 6a7a and 8a summarise the reported values for theyield strength obtained either during tension testswith superimposed pressure or after pressure soakingat the levels of hydrostatic pressure indicated Figures

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156 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullNill Cast and extruded 161

-[S)- - CP-NiAI Prepressurised 166

-EB - - - HP NAlP d 166- 1 repressunse

- -- - - - NiAI-NPrepressurised 166

50

300

(a)

1500

EB

(b)

middotmiddotlSI

__

middotEB

-bullbull-

bull

1000

-----------

1

500

_------------ --- -_---

Superimposed Hydrostatic Pressure MPa

100

50

20

00

o

c~ 15QJl-rj~ 10~8~ 05Z

oo 500 1000 1500

Superimposed Hydrostatic Pressure MPa

el~~ 200

250

o annealedp ~a~~a p ~a~~a p ~~~aT = 200degC 2h T = 400degC 2h

Strain

(c)d

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure c stress-strain curvesof polycrystalline NiAI tested in tension after annealing at 82JOC for 2 h pressurised to 14 GPa and tested at atmospheric pressure and afteraging pressurised specimens at either 200degC or 400degC for 2 h (Ref 159) (arrows show proportional limit) d dislocations being punched from Zrinclusion in NiAI pressurised to 1middot4 GPa (Refs 156 157 160 161)

7 Effect of pressure on yield strength of NiAI

of dislocations and a slight increase in the yieldstrength because of work hardening Little effect ofpressurisation was 0bserved on higher strengthPowder metallurgy produced NiAI (cf Fig7a

International Materials Reviews 1998 Vol 43 No4

and b)166 or W as well as arc-melted W (cf Fig6aand b) 72 in part due to the higher strengths of thematerials tested and the limited range of pressuresutilised

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 157

500

600(a)

Effects of pressure on work hardeningexponent nThe effects of testing with superimposed pressureon the work hardening exponent n have beeninfrequently studied Figure 9a and b illustrates theexperimentally measured effect of superimposed press-ure on n for a high strength aluminium alloy(7075- T651) tested in different orientations withrespect to the rolling direction Testing was conductedwith superimposed pressure on either uniaxial tensionspecimens or plane strain tension specimens andgenerally revealed an increase in n with increasingpressure The authors5051 indicated that such obser-vations could be related to the amount of secondphase particles which could punch out dislocationloops because of their smaller compressibility in amanner analogous to that described above for thecomposite materials

yield stress apparently arises because of pressureinduced dislocation generation around the reinforce-ment which increases significantly the local dislo-cation density thereby providing local hardening anda higher yield strength192195196 Transmission elec-tron microscope studies have confirmed that suchevents can occur provided the pressurisation is con-ducted at a large enough pressure to generate shearstresses of sufficient magnitude near the reinforce-ment192 Testing with superimposed pressure has alsobeen shown to inhibit the accumulation of damage(eg void initiation and growth) in such materials Asthe accumulation of damage reduces the load bearingarea and instantaneous modulus in such compositesand thereby reduces the strain hardening rate press-ure induced damage suppression has been proposedas also contributing to the elevated flow stressesobtained during tests conducted with superimposedpressure192196201 This point is further discussedbelow when summarising the effects of confiningpressure on the UTS In addition recent work hasalso shown that the level of residual stress in thematrix and reinforcement can be changed via pressur-isation343344 Finally various models315-320 have indi-cated that the presence of the non-deformingreinforcement particles provides constrained flow andenhances the flow stress of the matrix The super-position of pressure during tension testing shouldcounteract this effect as illustrated in a fewpapers318-320

15001000

== 0---

~ - - - ---= = = t0- -- - -

(b)

500Superimposed Hydrostatic Pressure MPa

oo

20

EZ 05-

- --6--- 2014AI-20SiCp 13 Jlm-AE 152201

-J - - 2014AI-20SiCp 13 Jlm-T6 152201

-1- - - 2124AI-14SiCw 1 Jlrn-UA 152201

-T---- 2124AI-14SiCw 1 ~m-OA 152201

-X - AI-AI Ni l~m 1523

0-- IIOOAJ-IOAI)O_~ 193

ltgt 193- -- 1100AI-15Al)0 -

- -0- - - 6061AI-15AJ 0 13lrn-UA 1952 3

-- -0- -- 6061AI-15AI 0 (13lm-OA 1952 3

- - -[SJ- - - 6061AI-15At) 0 13~ln-UA 185_ 3

- - -EB- - - 6090AI-25SiCp-SA 193

- - -- - - 6090AI-25SiCp-T6 193

-0- AZ91-19SiCp 15~lTn-T6 193

-e- AZ91-20SiCp52-lIn-T6 J93

c ~~~1-~ 200l x~ -X- X- y

100

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

8 Effect of pressure on yield strength ofdiscontinuously reinforced metal matrixcomposites

The largest changes in the yield strength obtainedeither after pressurisation or during tests with super-imposed pressure have been exhibited by compositematerials as shown in Fig 8a and b (Refs 152 185191-196 198 200 201) One source of the enhanced

Superimposed Hydrostatic Pressure MPa

00o 500 1000 1500 Effects of pressure on UTS

The experimental data for the UTS obtained viatension testing with a range of superimposed pressuresare provided for both monolithic metals as well ascomposites in Figs 10-15 As indicated above thestress state at the UTS (ie before necking) in suchspecimens consists of the uniaxial stress plus anysuperimposed hydrostatic pressure Data obtainedfrom some of Bridgmans original works are providedin Figs 10-13 for a variety of ferrous based systemsheat treated to different strength levels and micro-structures Figure 14a summarises similar data for avariety of other ferrous and non-ferrous structuralmaterials Figure 14b provides the ratio of the UTS

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158 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-6- _ TR uniaxialmiddotmiddotAmiddot TR plane strain-0 --- TW uniaxial

----e TW plane strain-0 - WRuniaxialbull - WRplanc strain

- --0 RW uniaxial- -+- - RW plane strain

-fSJ- Fe-034C-O75Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-045C-O83Mn-OO l6P-O035S-O19Si (as-received)

o normalised l650degF---0 annealed fine-grained- -6- annealed coarse-grained

- - - - - brine-quenchedtenlpered 600degF- - -+- - - brine-quenchedtempered 600degF-- -bull- - -- brine-quenchedtempered 900degF

015 3000

3000

middot11bull

1500 2000 25001000500Superimposed Hydrostatic Pressure MPa

o-- -0--

-6---e----+- -

--SJ-- Fe-O68C-O 7lMn-OO l3P-O025S-O19Si (as-received)

----0 --- Fe-O9C-O47Mn-O015P-O036S-OllSi (as-received)normalised 1650degFannealed fine-grainedannealed coarse-grainedbrine-quenchedspherodisedbrine-quenchedtempered 600degFbrine-quenchedtenlpered 900degF

bullbullbull

oo

2500

500

ce~E 1500rrJ~J 1000

10 Effect of pressure on UTS of various steelstested by Bridgman36

600

(a)

500 600

500

IImiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

middot0-middot -0

400

400

0

300

300

200

200

(b)

100

100Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

bullbull - A R bullbull

~ bull ~

000o

= 200Q)

=oc0lt

~ 150~=2

Q)C

100tt==~ 050eoZ 000

o

a n v hydrostatic pressure b normalised n v superimposedhydrostatic pressure

9 Effect of pressure on strain hardening exponentn of 7075AI- T651 (Refs 50 51)

3000

11 Effect of pressure on UTS of various steelstested by Bridgman36

Superimposed Hydrostatic Pressure MPa

500o

o -0

1500 2000 2500 30001000500

bullbull middot11II bull

~o Q ~omiddot omiddot

6 middot0middot omiddotmiddotmiddot=ltgt 6

1000

2500

ri1~ 1500J

~ 2000E

obtained at high pressure to that obtained at atmos-pheric pressure and a normalised UTS of 1middot0 indicatesno measurable effect of superimposed pressure onthe UTS The data for the monolithic metalsshown in Figs 10-13 as well as those summar-ised in Fig 14a and b indicate that superimposedpressure generally has a relatively minor effect on theUTS of most monolithic metals though someexceptions are shown Figure 15a and b illustratesthat composite materials often exhibit significantpressure dependent values for the UTS This hasbeen attributed152185189-201 to the pressure inducedsuppression of damage associated with the reinforce-ment and the matrix (eg void initiationgrowthcoalescence) which is covered in more detail in thefollowing sections on fracture behaviour

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 159

Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

A-+

bull -- -

0middot ------ -----()---6 - - - -

-8

iJII

-4-

-8-

---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

-8--- -lt)-

--

1000

5000

4000

C~ 3000~rJ5

2000 l-3~0

o S - - ~ lJS

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

I I I I I Iii I i

- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

3000

2500 -

d )000 f~~ -

~ 1500

~ middot_cmiddot- ~1000 ~_ibullbullbullbullbull~ - - -- - -- --0

s ti

500

12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure llPa

Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

- - -fr-

---]--

----T-

---0--

- - -lS -

------ - --(gt

--+-0-

4340 tempered 3000e 152

4340 tempered 5000e I 52

4340 tempered 7000e 152

01 Tool Steel Hard 152

01 Tool Steel Medium 152

01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

o 2124AI-14SiCw IJlm-UA 152201

bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

-+ Cu-28W 152

- - - -() - - - AI- Al Ni 152-

800

- - - -----------

~z~~~---~-----~bull-----~200

(a)

ts------6---1---------------- ------~

(b)

20

oo 100 WO ~O 400 ~O WO mo WO

Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

05

100

1000

1000

(a)

(b)

800

800600

600400

400

lZ91 19i

200

200Superimposed Hydrostatic Pressure MPa

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot-[H

----- ------0--middot- ----0

------6--- --6- ----------fJ--- --6

-----[S]----- ----[S]

-1-- - - - - - gtJ- - - - - - -Y- - -- - - -I- - - - - - gtJ

- -_~ ~~-~----- ~ _

middotmiddot~~-plusmn~middot~1middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

Superimposed Hydrostatic Pressure MPa

(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

~~ 1500

rJ5~ 1000

500

00

20

1500~~8 10l-o0Z

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000

categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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46 E ALADAG II L1 D PUGH and s V RADCLIFFE Acta lVletall1969 17 1467

47 c w A-DREWS Effects of pressure on terminal characteristicsof hexagonal metals PhD thesis Department of Metall-urgy and Materials Science Case Institute of TechnologyCleveland OH 1965

48 c w A-DREWS and s V RADCLIFFE Acta Metal 1966 1493749 c W A-DREWS and s V RADCLIFFE Acta lVfetall 1967 15 62350 1 P AUGER and D FRANCOIS Rev Phys Appl 1974 9 63751 J P AUGER and D FRANCOIS Int J Fract 1977 13 43152 A R AUSTEN and B AVITZUR J Eng Ind (Trans ASME)

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344 c LIU G MICHAL and J J LEWANDOWSKI in Residual stressesin composites measurement modeling and effects on thermo-mechanical behavior (ed E V Barrera et al) 1993 DenverCO TMS

345 P F THOMASON Ductile fracture of metals 1990 New YorkPergamon Press

346 J F KNOTT Fundamentals of fracture mechanics 1973London Butterworths

347 A W THOMPSON and J F KNOTT Metall Trans A 199324A523

348 R O RITCHIE and A W THOMPSON Metall Trans A 198516A233

349 F A McCLINTOCK and A S ARGON Mechanical behaviour ofmaterials 1966 Reading MA Addison-Wesley

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350 R O RITCHIE J F KNOTT and J R RICE J Mech Phys Solids1973 21 395

351 M F ASHBY J D EMBURY S H COOKSLEY and D TEIRLINCK

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1997 28A 2297354 J1 LEWANDOWSKI and J F KNOTT in Proc 7th Int Conf on

Strength of metals and alloys - ICSMA 7 Montreal Aug1985 1193 1985 New York Pergamon Press

355 J R LOW in Relation of properties to microstructure 1631953 Novelty OH ASM

356 A N STROH Adv Phys 1957 6418357 A N STROH Phios Mag 1958 3 597358 1 FREIDEL Dislocations 1964 New York Pergamon Press359 1 F KNOTT and A H COTTRELL J Iron Steel Inst 1963

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Moscow USSR365 1 1 LEWANDOWSKI and A W THOMPSON Metall Trans 1986

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1997 28A 389368 D TEIRLINCK F ZOK J D EMBURY and M F ASHBY Acta

Metall 1988 36 1213369 D TEIRLINCK M F ASHBY and J D EMBURY in Advances in

fracture research - ICF 6 New Delhi India Dec 1984 105New York Pergamon Press

370 w M GARRISON Jr and N R MOODY J Phys Chem Solids1987 48 1035

371 A W THOMPSON Metall Trans A 1987 18A 1877372 L M BROWN and J D EMBURY in Proc 3rd Int Conf on

Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

374 s H GOOD and L M BROWN Acta Metall 197927 1375 L M BROWN and w M STOBBS Phios Mag 197634 351376 P F THOMASON Ductile fracture of metals 94 1990 New

York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

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146 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

from differences in the thermal expansion coefficientbetween the matrix and the reinforcement in a com-posite In addition to providing experimental inputto various modelling efforts focusing on the funda-mentals of flow and fracture such information is alsorelevant to the formability of a material In this casethe broadest definition of formability relates to theability of the material to sustainaccommodate plasticflow often to very high levels of strain This caninclude such operations as rolling forging extrusionsheet metal forming etc While the formability deformability depends on a combination of factorsincluding the chemical composition microstructuretemperature and deformation velocity critical para-meters include the stress state and the superpositionof any residual stresses Since the stress state experi-mentally obtained where testing is conducted withsuperimposed hydrostatic pressure is closely relatedto that achieved (or desired) in many of the form-ing operations described above the data obtained(eg flow stress ductility etc) from such testing arevery relevant to the formability In addition many ofthe models for deformation processing require asinput the flow stress at very high values of strain Astesting with superimposed pressure typically increasesthe strain to fracture of many industrially importantmaterials to levels well beyond that obtained inuniaxial tension such large strain data can also beused as input for the various modelling efforts aimedat the forming operations described above

This review summarises the published experimentalobservations of the effects of superimposed hydro-static pressure on the mechanical behaviour obtainedunder quasistatic conditions for a variety of inorganicmaterials including recently obtained data on inter-metallics and metallic composites Although there isa body of similar literature on organic materials andceramic based systems this is beyond the scope ofthe present review However some relevant referenceshave been provided for the behaviour of organicmaterials202-235 which exhibit highly pressure sensitivebehaviour as well as for ceramic and geologic mater-ialsl71-181236-280tested with superimposed pressureThis review is divided into separate summaries andbegins with the testing techniques typically utilised instudies where quasi static loading conditions aredesired The effects of superimposed pressure on theflow fracture and deformation processing of a varietyof inorganic materials including intermetallics andcomposites follows The data summaries were pre-pared from published work on the various systemslisted while references to the original published worksare provided in the text as well as in each of theindividual data summaries The primary factors con-trolling flow and fracture will precede the presentationof the data summaries while the data summariesconclude with a short discussion of the major obser-vations Details of the various observations and issuesmay be found in the references cited

Experimental test techniques utilisedin high pressure testingHigh pressure mechanical testing13336 of struc-tural materials under quasistatic conditions has

International Materials Reviews 1998 Vol 43 NO4

Top plunger

Pressure gauge

Load cell

Specimen

Window

Support

Extension rod

High pressurecontainer

Bottom plunger

25mm

Schematic diagram of oil based high pressuredeformation apparatus3672 122 126269326-329

been conducted using a variety of high pressuremedia including solid171-174179249251273277326327liquids36122126269326-329and gases271273330The lasttwo groups are typically preferred as non-hydrostaticconditions may exist with solid media Typical liquidmedia include a variety of oils as well as kerosenepentane and naphtha while gas media include inertgases (eg Ar He) and hydrogen Pressure levels inexcess of 3 GPa have been obtained with such sys-tems High pressure tests well in excess of 3 GPa havebeen conducted using diamond anvil cells326327331and other test systems where the volume of materialtested in such studies is typically too small to sampleenough of the material to be of use to the structuralmaterials community where size effects on materialproperties have been observed Significantly higherpressure (eg gt 10 GPa) may be present in variousshock loading experiments conducted under impactor high velocity experiments as reviewed elsewhere325and not covered in this review The liquid mediasystems utilised in quasistatic testing are typicallylimited to use below 300degC because of the potentialdecompositioncracking of the oil while the solid-and gas-based systems have been utilised at gt 1000degCThis review focuses primarily on data obtained oneither oil- or gas-based systems and those opera-ted at relatively modest (eg lt 300degC) temperaturesthough references to tests conducted at high pressureand high temperature are provided (Refs 171-181236-244 246 247 251-253 255 258 260-262 264

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 147

pressure vessel mantle

7y 6_10_m_m f-pressure vessel liner

servohydraulicactuator bull

argon gas line

a internal load cellb specimen

2 Schematic diagram of gas based high pressure deformation apparatus271273330334

265 268 269 271-273 276-278) References to theeffects of superimposed pressure on creep265281-286have also been provided though this aspect is notcovered in this review

Pressure generation in the oil based systems ofteninvolves compression of the fluid in a pressure vesselvia pressing a plunger in to the bore of a pressurevessel as shown in Fig 1 Pressure is typically moni-tored via the use of a manganin coil pressure gaugethat is exposed to the high pressure environmentManganin coils are used in this case because of thehighly reproducible and linear manner with whichthe resistance of the coil varies with changes inpressure22332 Simple pressurisation experiments canbe conducted with such systems whereby a materialis placed into the pressure vessel and the fluid (ieoil) is compressed to produce a measurable level ofhydrostatic pressure In such simple pressurisationstudies the pressure is subsequently reducedremovedin order to measure the resulting behaviour of thematerial at atmospheric pressure Typically both thepressurisation rate and depressurisation rate aremonitored and kept at a constant low value becauseof the possibility of significant specimen heating (orcooling) during the pressurisation (depressurisation)cycles

Mechanical testing with superimposed hydrostaticpressure has also been conducted on similar devicesto that shown in Fig 1 In these cases the specimenis typically inserted into the load train assemblypresent in the pressure vessel shown in Fig 1 followedby pressurisation of the fluid and the subsequenttension (or compression) testing of the specimen atthe desired level of superimposed hydrostatic pressureIn such tests the high pressure fluid has access to allsurfaces of the specimen It is important to monitorcontinuously (and keep constant) the pressure dur-ing the test in addition to having the capabilityto monitor accurately the load and displacementrequired to deform the specimen under pressure aspointed out elsewhere33o In oil based pressure systemssuch as that shown in Fig 1 the confining (iehydrostatic) pressure is kept constant via either using

an intensifier or retracting the bottom hydraulicpiston while inserting the top plunger In such testingthe use of external load cells (ie positioned on theload train but outside of the pressure vessel) mayproduce erroneous data for the load required todeform the specimen because of the variable amountof seal friction which results during the generation ofpressure in the chamber In an attempt to determinethe load on the specimen inside the vessel moreaccurately pressure compensated load cells consistingof a measuring load cell and a compensating loadcell were developed330333 as shown schematicallyin Fig 1 Displacement andor strain measurementin such studies has typically relied on monitor-ing piston displacement though more recentstudies103 155-157161-163189190192-195197have utilisedpressure compensated strain gauges affixed to thespecimen surfaces In some studies195197213the press-ure vessel was fitted with machined cross-bores andtransparent quartz windows as shown in Fig 1 whichenabled in situ monitoring of deformation and thedevelopment of necks under pressure

Gas based systems like that shown schematicallyin Fig 2 typically utilise a pressure intensifier togenerate pressure that is contained within a multi-walled pressure vessel where the volume of gas pre-sent at high pressure in the vessel is kept as low aspossible because of the danger associated with thestored energy Such systems often utilise many of thesame types of diagnostic techniques as that describedabove though direct visual monitoring of the speci-men during deformation has not been conductedbecause of the inherently higher danger associatedwith gas based systems Pressure fluctuations duringmechanical testing in gas based systems are typicallymuch less than those of the oil based systems wherethe pressure generation techniquedevice is directlylinked to the piston which controls displacement ofthe specimen

Tables 1 and 2 summarise many of the variousinvestigators that have utilised high pressure testingto evaluate the mechanical behaviour of materialsTable 1 summarises the maximum pressure utilised

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 149

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150 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Table 2 Summary of investigations on effects of hydrostatic pressure on mechanical behaviour ofinorganic materials - categorised by class of material

Pressu re range

Materials Researcher(s) Failure mode P MPa Measured properties Note

0-27 (UTS) Ef

Ef

Ef

0-15 (UTS) Ef void fraction0-19 (UTS) Ef void fraction

PrepressurisedprestrainedTemperature upto 600aC

Prepressurised

Prepressurisedprestrained

Interrupted testInterrupted test

Prepressurised

Prepressu rised

Prepressu rised

PrestrainedPrepressurised

Interrupted test

Prepressu rised

ay af poundf

ay

ay af EI

ay UTS 8f

Ef

(Iy af poundf

ay af EI

Ef

ay Ef EI n K1c

EI

Ef

Ef

qEf

dadn versus ~Kaf Ef

ay UTS Ef

(Iy UTS qay Ef

(Iy Ef voids quantification

ay af Ef

Ef

ay UTS nEf voids quantification(Iy af qay

ay

dadn versus ~Kay UTS Ef

ay

ay

ay (If Ef

ay UTS Ef

ay UTS Ef

Ef

ay EIEf

ay Ef

Ef

J

CRSS

0-58

0-12

0-270-12

0-7S

0-26

030-110-08

0-330-170-200-08

0-120-110-1S01-020-070-36

OS

0-103

01-500

01-3060

01-290001-S0001-140001-50002000

01-250001-31001000

01-600

01-6900-48001-60001-600

01-20001-296001-35001-80001-900

01-300

01-60001-52001-30001-62001-3501-92001-69001-69001-300

01-110001-60001-7

01-110001-S0001-69001-345100001-2250

01-70001-90001-345150001-69050017201-210001-126001-110017201-110001-110001-3501-69001-110001-110017201-69001-970

Cleavage

Cleavage

MVCshear

MVCshear

MVCshearMVCshear

ShearMVC

Intergranular

MVC

MVCshearMVCshear

MVCshear

MVCdelamMVCshear

MVCshear

MVCshear

MVCshear

Nishihara et al114

French and Weinrich89

Pugh and Green 123

Vajima et al149

Pugh and Green 123

Plumbridge et af121

HU93

ZOk152

ZOk152

Lewandowski etal189190

Liu andLewa ndowski103 195

Korbel et al99

Auger and Francois5051

Franklin et al84

Bridgman36

Ball et al53

Bullen et al64

Mellor and Wronski108

French andWeinrich88141

Vajima et al149

Pugh and Green 123

French and Weinrich85

Weinrich andFrench85141

Omura119

Bridgman36

ZOk152

Vajima et al149

Vajima et al149

Bridgman36

Dobromyslov et af79

Galli and Gibbs90

Kuvaldin et af100

Mellor and Wronski108

Spitzig 135

Vajima and Ishii147148

Vajima et al149

Ohmori et al118

Bullen et al65

Davidson andAnsell7576

Vajima et af149

Itoh et al95

Ohmori et al118

Worthington 144

Pugh and Green 123

Wagner et al140

Johnson et al97

Davidson et af74

McCann et al106

Brownrigg et al63

Johnson et af97

Spitzig et al133

Spitzig et al133

Plumbridge et al121

ZOk152

Spitzig et al134

Spitzig et al134

Johnson et al97

Zok and Embury152153

ZOk152

MoMoMoMoMo

7075AI-T47075AI-T6517075AI

Cu alloysPure

PureERCH CuLeaded brassa-brass a-fJ brass

70-30 40-60 brassy-brassCu-002BiCu-(15-40)ZnCu-(45-97)Ge

Ni alloyPure

bcc metalsCrCrCr

Mo

Fe-(O02-049)CMild steel (OOSC)Mild steel (O14C)Fe-3SiCast ironsSpheroidised cast iron101S steel1045 steel1045 steel1045 steel (spheroidised)4130 steel4310 steel4330 steel4360 steel4340 steelMaraging steelHV SO steelHV 130170180 steels01 tool steelTi-V steel

AI alloysPurePurePureAI-1 Si-07Mg-04MnAI-Cu-Mg-Si61S AI-T42014AI-T6AE2124AI-UAOAMB85-UAOA

6061AI-UAOA

Metals

Ferrous alloysSingle crystal FePure FePure FePure FeArmco FeFe-(0004-11)C

Mo Robbins andWronski131132

Cleavage 01-500

CRSS critical resolved shear stress delam delamination dadn crack propagation rate EI elongation HV Vickers hardness J J-integral MVC microvoidcoalescence UTS ultimate tensile strength

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 151

Table 2 (cant)

Pressure range

Materials Researcher(s) Failure mode P MPa Pj(fy Measured properties Note

Metalsbee metalsNb Bridgman36 01-2850 (ff qTa Bridgman36 01-2850 (ff [f

Ta Nishihara et al114 01-500 ayUTS rof Temperature upto 600C

Ta Robbins and Wronski131 1500 (fy Prepressu rised0-500

W Bridgman36 01-2840 af lofW Das and Radcliffe73 01-1100 0-15 (ff af lofW Daga71 01-1100 0-20 ay (ff qW Davidson et al74 CleavageMVCjshear 01-1600 qW Mellor and Wronski108 2800 (fy af EI Prepressu rised

prestrainedhcp metalsBe (PM) Aladag45 Intergranularj 01-980 af [f

Aldag et al46 transgranularBe (PM) Andrews and 01-2700 Prepressurised

Radcliffe49Be (ingot) Aladag45 Transgranular 01-980 0-38 (fy af [f

Aldag et al46

Be (castrolled) Bedere et al55 Intergranularj 01-1500 0-122 (ly af [f

transgranular shearCd Nakajima et al111 01-600 ayCo Davidson et al74 CleavagejMVCjshear 01-2350 f~Mg Davidson et aJ74 MVCjshear 01-1800 4Mg Pugh and Green 123 01-460 [fAZ91 (PM) Lahaie et al101 Intergranularshear 01-690 0-22 (fy ltofAZ91-T4jT6 Lewandowski et al193 01-380 af (f

Zn Davidson et al74 Brittlejplastic rupture qZn Pugh and Green 123 Cleavageplastic 01-138 ay q

ruptureZn-41AI Pugh and Green 123 01-410 ltofTi-7 AI-2Nb-1Ta (x) Johnson et al97 172 02 ay af lt1 Prepressu risedTi-6AI-4V (ajm Johnson et al97 172 02 (fy (ff Gf Prepressu risedTi-13V-l1 Cr-3AI (x) Johnson et al97 172 0middot2 ay af q Prepressurised

Metal matrix composites

AI matrix2014-20SiCp-T6jAE ZOk152 MVCshear 01-980 0-24 ay UTS Gf

2124-14SiCw-UAjOA ZOk152 MVCshear 01-690 0-20 ay UTS l12014-20SiCp-T6jAE Mahon et al198 MVCjshear 01-980 0-24 ay UTS l12124-14SiCw-UAjOA Vasudevan et al201 MVCjshear 01-690 0-20 ay UTS [f

MB85-15SiCp-UAjOA Lewandowski MVC 01-300 0-08 (ly af (fet al189190

M B85-15SiCp-UAjOA Liu 195 MVC 01-300 0-08 ay (ff q6061AI-15AI203-UAjOA Liu et al194195197 MVC 01-300 0-11 ay af q Damage

quantification6090AI-25AI203-SAjT6 Lewandowski et al193 MVC 01-400 GfMB78-15SiCp-UAjOA Singh and MVC 01-500 q Damage

Lewandowski199 quantificationA356-1 Oj20SiCp- T6 Embury et al184 MVC 01-850 q Damage

quantificationAI-AI3Ni Zok 152 MVC 01-690 0-45 ay UTS lt1

Mg matrixAZ91-20SiCp-T4 Lewandowski et al193 01-350 0-12 GfAZ91-19SiCp15 llm-T6 Lewandowski et al193 MVC 01-440 0-14 ay UTS af [f Damage

quantificationAZ91-20SiCp52 llm-T6 Lewandowski et al193 MVC 01-490 0-19 ay UTS af [f Damage

quantificationCu matrixCu-28W Zok152 MVC 01-690 UTSq

IntermetallicsNiAI Margevicius and Transgranularj 01-1400 0-140 (ly (ff Gf wj

Lewandowski155161163 inte rg ra nul ar PrepressurisedNiAI Weaver et al166167 Prepressu risedNi3AI Zok et al152170 Intergranular 01-965 af GfAI3Ti Witczak and Varin 169 2000 ay af lof HV PrepressurisedAmorphous metalsPd Cu Si Davis and Kavesh323 Shear 01-690 0-047 af EfZr Ti Ni Cu Be Lewandowski et al324 Shear 01-650 0-035 af Ff

CeramicsAI203 Bridgman36 2350-2960 afB203 Bridgman3637 2350-2960 af Gf density changeLiF Hanafee and 01-1300 Dislocation velocity

Radcliffe 176MgO Weaver and Brittlejshear 01-1000 ay af Ff

Paterson 180181NaCI Bridgman36 2350-2960 af [f

CRSS critical resolved shear stress delam delamination dajdn crack propagation rate EI elongation HV Vickers hardness J J-integral MVC microvoidcoalescence UTS ultimate tensile strength

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152 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

and any pressure variation reported during the testin addition to the load and strain measurementtechniques reported by the various investigators onthe materials listed Table 2 provides a similar list ofinvestigations organised by the type of material (egmetal intermetallic composite) tested as well as bythe crystal structure (eg bcc fcc hcp) of the metalsunder investigation Included in Table 2 are thespecific properties measured by each of the investi-gators and any comments related to the failure modespresent References to the works in Tables 1 and 2are provided while the specific data summariesappear in subsequent figures In most of the studieswhere testing is conducted with superimposed hydro-static pressure the specimens have been coated orjacketed274 with some impervious membrane (egpolymer Cu shrink fit tubing etc) in order to preventingress of the pressure medium into any surfacecracks porosity etc274 The membrane utilised istypically very thin and does not contribute signifi-cantly to the load bearing area of the specimenFurthermore pressurisation of specimens shieldedwith such membranes in and of itself has not pro-duced changes to the subsequent flow stress obtainedat atmospheric pressure

1

-2-1

o~ 1cr

2

3 Yield surface plotted in principal stress spacefor fully dense isotropic and homogeneousmaterial335336

(2)

(4)

(5)

ka = 511 + 512 + S13

kc = 2S13 + 533

shear stresses developed owing to the differences incompressibility between the matrix and the secondphase128 The maximum shear stress [max at thematrixsecond phase interface has been separatelyestimated by Das and Radcliffe73 and Ashby et al337

for a spherical particle and is given by

3Gm ( Km -Kp )[max = K 3K + 4G pm p m

where Gm is the shear modulus of the matrix Km

and K the bulk moduli of the matrix and the sec-ond phase respectively and P the applied hydro-static pressure Dislocations are generated when[max reaches the nucleation stress for dislocationgeneration which can be theoretically predicted ordetermined experimen tally338

Another manner in which shear stresses are gener-ated in polycrystalline materials through the simpleapplication of hydrostatic pressure is through theanisotropy of elastic constants91128 Crystals of allsystems except the cubic system can change shapewhen subjected to hydrostatic pressure cubic crystalshave isotropic bulk moduli The volume compress-ibility which is the inverse of the bulk modulus isthe pressure induced change in volume of a crystalnormalised to its original volume and the linearcompressibility k is the amount of pressure inducedlength change in a straight line normalised to itsoriginal length For the cubic system k is independentof orientation and is related to the elastic compliance5ij through

k = 511 + S12 bull bull bullbull bull (3)For the trigonal hexagonal and tetragonal systemstwo constants are required the value in the a directionka and the value in the c direction kc These compress-ibilities are related to the elastic compliance 5ij by

Effects of superimposed pressure onstress state in cylindrical specimensConditions present before necking incylindrical specimensPlastic deformation in metallic systems tested at lowhomologous temperatures primarily occurs via dislo-cation generation andor movement via shear stressesoften referred to as conservative motion or glidePlastic deformation under such conditions occurswhen the effective stress (j equals the yield strengthin tension (Jy where the effective stress is given as

- 1 ( )2 ( )2 ( )2] 120=0[(J1-(J2 + 02-(J3 + (J3-(J1

(1)and (Jb (J2 and (J3 represent the principal stressesThe application of a purely hydrostatic stress (ie(J1 = 02 = (J3) produces no shear stress in a homo-geneous and isotropic material as shown by the 3-Dyield surface plotted in stress space in Fig 3 Ahydrostatic stress is represented as the axis of thecylinder in Fig 3 and since such stresses never touchthe yield surface there should be no effect ofpressurisationpressure soaking on the subsequentflow behaviour when uniaxial testing is conducted atatmospheric pressure Pressurisation in this casedenotes the simple application of hydrostatic pressureto a material and its subsequent removal Thereshould similarly be little effect of superimposed press-ure on yielding when testing is conducted on acylindrical specimen in the presence of a confining(ie hydrostatic) pressure as the stress state up to theultimate tensile stress (UTS) (ie before necking) insuch specimens consists of the uniaxial stress plusany superimposed hydrostatic pressure

However simple pressurisation can serve as ameans for generating dislocations in a materialaround inclusions and other defects as there are local

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 153

1

4 Yield surface plotted in principal stress spacefor material containing void fraction of a 0057and b 0180 (Ref 336)

1

1

a~l 05cr

o~ta

-05

-1

-1

(a)

(b)

The linear compressibility in any other direction kris given by

kr = ka + (ke - ka)r2 (6)

where r is the direction cosine with subject to thec axis

If non-cubic metals can change shape because ofpressurisation then a random aggregate of manycrystals when subjected to unit hydrostatic pressurewill develop shear stresses across grain boundaries Itis this shear stress which produces dislocation gener-ation in anisotropic materials

The degree of anisotropy in these non-cubic systemsis given in terms of the ratio keka The anisotropy ofa number of hexagonal metals is given in Table 3Those metals with a high degree of anisotropy Cdand Zn have been shown91339 to require only modestlevels of pressure ( 300 MPa) to induce plastic strainin the grains while metals with ratios close to one(where a cubic metal equals 10) Zr and Mg requiredthe highest pressures ( 2middot6 GPa) to produce onlytrace amounts of plastic deformation Although TEManalyses have confirmed the presence of pressureinduced dislocations around inclusions in less pureFe and Fe-C alloys containing inclusions65139 highpurity cubic metals such as Cu AI Fe and Ni haveshown no such plastic deformation after pressuris-ation to levels up to 1 GPa (Refs 109 339)

Porous materials consisting of either interconnectedor isolated pores are also highly pressure sensitive340provided the pressure medium is shielded from thespecimen to prevent ingress of the pressure medium(ie gas liquid) into the pores The 3-D yield loci forsuch materials are distinctly different from that shownin Fig 3 for homogeneous and isotropic materialsShown in Fig 4 are 3-D yield loci for porous materialscontaining increasing levels of porosity335336341342It is clear that the application of a hydrostatic pressureof sufficient magnitude in these cases can touch theyield surface and thereby produce plastic flowExamples of such effects are provided in works onporous Fe (Refs 62 137)

where Oflow is the flow stress a the minimum specimenradius R the radius of curvature at the neck or notchand rn the distance from the centre along the planeof the neck

Since the notchneck geometry will often changewith additional deformation the level of triaxialtensile stress resulting from deformation of such

International Materials Reviews 1998 Vol 43 NO4

mens) when subsequently tested in tension also experi-ence triaxial tensile stresses in the neckednotchedregion In this case the major difference between thenecked region which evolved during deformation andthat simulated by prenotching a pristine (ie non-deformed) specimen relates to the differences indeformation history (and any damage) present in thenecked region as compared to the notched regionBridgman provided an estimate of the additionalhydrostatic tension OT in the plane of a neck ornotch2436 as

Conditions present past necking incylindrical specimensOnce a neck begins to form in a cylindrical tensilespecimen tested at atmospheric pressure triaxialtensile stresses develop in the necked region Boththe magnitude and location of such triaxial stressesvary with location in the neck which develops withadditional deformation Prenecked (eg notched speci-

Table 3 Linear compressibility and anisotropyfactors for some non-cubic materials(Refs 128 339)

Lattice ratioLinear compressibility MPa

Metal cia c axis ke a axis ka Ratio keka

Cadmium 18856 1890 x 106 217 X 106 870Zinc 18564 1341 x 106 201 X 106 670Bismuth 26095 1645 x 106 684 X 106 240Magnesium 16235 1016 x 106 1016 X 106 1middot00Zirconium 1middot5931 380 x 106 3middot80 X 106 1middot00Titanium 15870 270 x 106 270 X 106 100Beryllium 15684 227 x 106 291 X 106 078

(a 12 )

OT = Oflow In 1 + 2R - 2a~ (7)

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154 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Superimposed Hydrostatic Pressure MPa

4340 tenlpered 3000C 152

4340 tempered (eQ 5000C 152

4340 tempered 7000C 152

o 4310-Lower Yield 133

bullbull 4330-Lower Yield 113

6 01 Tool Steel Hard 152

6 01 Tool Steel Mediunl 152

6 01 Tool Steel Soft 152

[S ri-V Steel 9500C FRT 152

fpound Ti-V Steel 700degC FRT 15~

bull 7075AI-T651(TR) 5051

bull 7075AI-T65 I(WR) 5051

T 7075AI-T65I (RW) 5051

() 201411 1(21)

EE BY -80 1ower Yield 134

bull Maraging-Unaged (Ten) 134

bull Maraging-Unaged (Comp) ]34

bull Maraging-Aged (Ten) 134

bull1200

(a)

bullbull

1000

EB

[SJ

800600400200

bull bull bull bullbullbullII bullbull JI bullbull Q bullbull bull

~ 6III II II bull

j 6 i i6

o

20

o

=~~ 15Q)~~

rJ)

0

~ 10~

e~ 05Z

~~ 1500

2000

=~eJ)

~ 1000~~

rJ)

e-Q)

~

00(b)

(gt 2124J() () I

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure

5 Effect of pressure on yield strength of various bee and fcc metallic alloys

specimens will vary past necking in the cylindricalspecimen Thus while the level of superimposedhydrostatic pressure has been kept relatively constantin many of the studies listed in Tables 1 and 2 thetriaxial stresses present in the neck during tests withsuperimposed pressure will depend on a variety offactors including the neck geometry level of superim-posed pressure and the flow stress of the materialIt is important to note that some studies investigat-ing the effects of superimposed pressure on tensiontests have been conducted under conditions suchthat compressive triaxial stresses were present in thenecked region In these cases the levels of superim-posed pressure were high enough to overcome thetriaxial tensile stresses which developed in the evolv-ing neck Thus the ability to monitor visually thedevelopment of the neck during tests with superim-posed pressure as described above or conductinginterrupted tests where the neck can be physicallymeasured outside of the high pressure environmenthas some merits858689103197213

Effects of superimposed pressure onflow behaviourEffects of superimposed pressure onyield stressFigures 5-8 summarise published data on the effectsof pressurisationpressure soaking as well as tensiletesting at different levels of superimposed hydrostaticpressure on the yield strength typically reported asthe 0middot2 offset yield strength In the former tests theyield strength was measured at atmospheric pressureafter pressurisation while the measurements of yieldstress in the latter cases occurred during tensile testsconducted with superimposed hydrostatic pressureThe pressure medium utilised in the studies summar-ised was either an oil medium or Ar gas and wasconfirmed to be hydrostatic Figure 5 summarisesdata obtained on a variety of steels and aluminiumalloys while Fig 6 shows similar data obtained on avariety of single phase metals possessing a bcc crystalstructure Figure 7 is a plot of the same type of

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 155

___bull __ Ar111co Iron 65

5b 6b 7b and 8b are plots of the ratio of the yieldstrength obtained at pressure (or after pressure soak-ing) to that of the control material (ie no pressuresoaking) in the manner utilised by a number ofinvestigators henceforth this is called the normalisedyield strength Pressure independent yielding is rep-resented by the horizontal line at 1middot0 for the normal-ised yield strength in Figs 5b-8b It is clear fromFig 5a that a number of conventional structuralmetallic alloys exhibit nominally pressure independ-ent yielding behaviour as predicted by equation (1)Slight positive deviations for monolithic materials (ienormalised yield strengthgt 1 in Fig 5b) have beenexplained as in part due to the pressure depend-ence of the shear modulus which though modestis non-zero for various metallic materials136Models313314 have been developed to predict suchpressure dependent yielding in metallic materials andmetallic glasses321-323 and a few studies have invokedsuch models to explain such pressure dependence ofthe yield stress136 It should be noted that there havebeen observations of materials which exhibit muchgreater positive deviations than those of the monolithicmetals summarised in Fig 5a and b For example ithas been clearly shown that superimposed pressuresignificantly inhibits dislocation mobility in LiFthereby elevating the flow stress above that obtainedat atmospheric pressure176

It is also clear that some of the monolithic metalsshown in Fig 5a and b as well as a variety of bccmetals (cf Fig 6a and b) and certain chemistries ofthe intermetallic NiAI shown in Fig7a and b ex-hibit a significant decrease in the yield strength afterpressure soaking or during tests conducted withsuperimposed pressure In these cases the materialstypically exhibited a yield point and Liiders exten-sion before pressure soaking or testing with superim-posed pressure Pressurisation (andor testing withpressure) was shown to remove the yield pointand Liiders strain and thereby reduce the yieldstrength155157159161162166167as illustrated for castextruded NiAI in Fig 7c As shown in Figs 6a andband 7a and b large reductions in yield strengthwere obtained in Fe (Refs 65 147) Cr (Refs 59 6466 72) and commercially pure NiAI (Refs 155 157161-163) that had been cast and extruded ExtensiveTEM analyses in these cases revealed that pressureinduced dislocation generation occurred at non-metallic inclusions and other inhomogeneities in thesematerials6465155157158161an example of which isshown in Fig 7d (Ref 157) The generation of thesemobile pressure induced dislocations thereby reducedthe yield strength while subsequent thermal agingstudies conducted for sufficient time-temperaturecombinations at atmospheric pressure enabled relock-ing of the dislocations by interstitial impurities (egC) and a return of the yield point and Liidersstrain6465107147166as illustrated for NiAI in Fig7c(Ref 159) Similar studies166167 conducted on highpurity NiAI failed to reveal a yield point and anysubsequent effect of pressurisation on the yield stressas shown in Fig 7a and b consistent with sucharguments Pressurisation of the largest grained Fein Fig 6a and b (Ref 147) to increasingly higherpressures eventually produced excessive generation

International Materials Reviews 1998 Vol 43 NO4

1200

(a)

(b)

---)

1000800600

~_-----1-~ - --

400200

- - Chromium 64

bull - Iodide Chromium 72

Superimposed Hydrostatic Pressure MPa

bull ~ ~- Y- -y_~~~ - - -9

-------

cOil 15cQJ

000 10~~5 050Z

000

800

eo 700~~ 600pound 500eiJcCJ 400V)

0 300~~ 200

100o

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

20

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

6 Effeet of pressure on yield strength of variousbee metals GS grain size

--0 Fc GS=11Jlnl 147

-0 Fe GS=14Jlm 147

-[S- Fe GS=19Jlm 147

-83- - Fe GS=30Jlm 147

-- - Fe GS=450~lIn 147

6 - - PM T 72- ungsten

-pound --Arc-Melted Tunsten 72

information for the intermetallic NiAI which possessesa B2 (ie bcc derivative) crystal structure while Fig 8is a plot of data from more recent work on compositesbased on either aluminium or magnesium alloymatrixes The data reported for the control materials(ie no pressure soaking) occur on the ordinate at0middot1 MPa (ie atmospheric pressure) Figures 5a 6a7a and 8a summarise the reported values for theyield strength obtained either during tension testswith superimposed pressure or after pressure soakingat the levels of hydrostatic pressure indicated Figures

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156 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullNill Cast and extruded 161

-[S)- - CP-NiAI Prepressurised 166

-EB - - - HP NAlP d 166- 1 repressunse

- -- - - - NiAI-NPrepressurised 166

50

300

(a)

1500

EB

(b)

middotmiddotlSI

__

middotEB

-bullbull-

bull

1000

-----------

1

500

_------------ --- -_---

Superimposed Hydrostatic Pressure MPa

100

50

20

00

o

c~ 15QJl-rj~ 10~8~ 05Z

oo 500 1000 1500

Superimposed Hydrostatic Pressure MPa

el~~ 200

250

o annealedp ~a~~a p ~a~~a p ~~~aT = 200degC 2h T = 400degC 2h

Strain

(c)d

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure c stress-strain curvesof polycrystalline NiAI tested in tension after annealing at 82JOC for 2 h pressurised to 14 GPa and tested at atmospheric pressure and afteraging pressurised specimens at either 200degC or 400degC for 2 h (Ref 159) (arrows show proportional limit) d dislocations being punched from Zrinclusion in NiAI pressurised to 1middot4 GPa (Refs 156 157 160 161)

7 Effect of pressure on yield strength of NiAI

of dislocations and a slight increase in the yieldstrength because of work hardening Little effect ofpressurisation was 0bserved on higher strengthPowder metallurgy produced NiAI (cf Fig7a

International Materials Reviews 1998 Vol 43 No4

and b)166 or W as well as arc-melted W (cf Fig6aand b) 72 in part due to the higher strengths of thematerials tested and the limited range of pressuresutilised

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 157

500

600(a)

Effects of pressure on work hardeningexponent nThe effects of testing with superimposed pressureon the work hardening exponent n have beeninfrequently studied Figure 9a and b illustrates theexperimentally measured effect of superimposed press-ure on n for a high strength aluminium alloy(7075- T651) tested in different orientations withrespect to the rolling direction Testing was conductedwith superimposed pressure on either uniaxial tensionspecimens or plane strain tension specimens andgenerally revealed an increase in n with increasingpressure The authors5051 indicated that such obser-vations could be related to the amount of secondphase particles which could punch out dislocationloops because of their smaller compressibility in amanner analogous to that described above for thecomposite materials

yield stress apparently arises because of pressureinduced dislocation generation around the reinforce-ment which increases significantly the local dislo-cation density thereby providing local hardening anda higher yield strength192195196 Transmission elec-tron microscope studies have confirmed that suchevents can occur provided the pressurisation is con-ducted at a large enough pressure to generate shearstresses of sufficient magnitude near the reinforce-ment192 Testing with superimposed pressure has alsobeen shown to inhibit the accumulation of damage(eg void initiation and growth) in such materials Asthe accumulation of damage reduces the load bearingarea and instantaneous modulus in such compositesand thereby reduces the strain hardening rate press-ure induced damage suppression has been proposedas also contributing to the elevated flow stressesobtained during tests conducted with superimposedpressure192196201 This point is further discussedbelow when summarising the effects of confiningpressure on the UTS In addition recent work hasalso shown that the level of residual stress in thematrix and reinforcement can be changed via pressur-isation343344 Finally various models315-320 have indi-cated that the presence of the non-deformingreinforcement particles provides constrained flow andenhances the flow stress of the matrix The super-position of pressure during tension testing shouldcounteract this effect as illustrated in a fewpapers318-320

15001000

== 0---

~ - - - ---= = = t0- -- - -

(b)

500Superimposed Hydrostatic Pressure MPa

oo

20

EZ 05-

- --6--- 2014AI-20SiCp 13 Jlm-AE 152201

-J - - 2014AI-20SiCp 13 Jlm-T6 152201

-1- - - 2124AI-14SiCw 1 Jlrn-UA 152201

-T---- 2124AI-14SiCw 1 ~m-OA 152201

-X - AI-AI Ni l~m 1523

0-- IIOOAJ-IOAI)O_~ 193

ltgt 193- -- 1100AI-15Al)0 -

- -0- - - 6061AI-15AJ 0 13lrn-UA 1952 3

-- -0- -- 6061AI-15AI 0 (13lm-OA 1952 3

- - -[SJ- - - 6061AI-15At) 0 13~ln-UA 185_ 3

- - -EB- - - 6090AI-25SiCp-SA 193

- - -- - - 6090AI-25SiCp-T6 193

-0- AZ91-19SiCp 15~lTn-T6 193

-e- AZ91-20SiCp52-lIn-T6 J93

c ~~~1-~ 200l x~ -X- X- y

100

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

8 Effect of pressure on yield strength ofdiscontinuously reinforced metal matrixcomposites

The largest changes in the yield strength obtainedeither after pressurisation or during tests with super-imposed pressure have been exhibited by compositematerials as shown in Fig 8a and b (Refs 152 185191-196 198 200 201) One source of the enhanced

Superimposed Hydrostatic Pressure MPa

00o 500 1000 1500 Effects of pressure on UTS

The experimental data for the UTS obtained viatension testing with a range of superimposed pressuresare provided for both monolithic metals as well ascomposites in Figs 10-15 As indicated above thestress state at the UTS (ie before necking) in suchspecimens consists of the uniaxial stress plus anysuperimposed hydrostatic pressure Data obtainedfrom some of Bridgmans original works are providedin Figs 10-13 for a variety of ferrous based systemsheat treated to different strength levels and micro-structures Figure 14a summarises similar data for avariety of other ferrous and non-ferrous structuralmaterials Figure 14b provides the ratio of the UTS

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158 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-6- _ TR uniaxialmiddotmiddotAmiddot TR plane strain-0 --- TW uniaxial

----e TW plane strain-0 - WRuniaxialbull - WRplanc strain

- --0 RW uniaxial- -+- - RW plane strain

-fSJ- Fe-034C-O75Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-045C-O83Mn-OO l6P-O035S-O19Si (as-received)

o normalised l650degF---0 annealed fine-grained- -6- annealed coarse-grained

- - - - - brine-quenchedtenlpered 600degF- - -+- - - brine-quenchedtempered 600degF-- -bull- - -- brine-quenchedtempered 900degF

015 3000

3000

middot11bull

1500 2000 25001000500Superimposed Hydrostatic Pressure MPa

o-- -0--

-6---e----+- -

--SJ-- Fe-O68C-O 7lMn-OO l3P-O025S-O19Si (as-received)

----0 --- Fe-O9C-O47Mn-O015P-O036S-OllSi (as-received)normalised 1650degFannealed fine-grainedannealed coarse-grainedbrine-quenchedspherodisedbrine-quenchedtempered 600degFbrine-quenchedtenlpered 900degF

bullbullbull

oo

2500

500

ce~E 1500rrJ~J 1000

10 Effect of pressure on UTS of various steelstested by Bridgman36

600

(a)

500 600

500

IImiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

middot0-middot -0

400

400

0

300

300

200

200

(b)

100

100Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

bullbull - A R bullbull

~ bull ~

000o

= 200Q)

=oc0lt

~ 150~=2

Q)C

100tt==~ 050eoZ 000

o

a n v hydrostatic pressure b normalised n v superimposedhydrostatic pressure

9 Effect of pressure on strain hardening exponentn of 7075AI- T651 (Refs 50 51)

3000

11 Effect of pressure on UTS of various steelstested by Bridgman36

Superimposed Hydrostatic Pressure MPa

500o

o -0

1500 2000 2500 30001000500

bullbull middot11II bull

~o Q ~omiddot omiddot

6 middot0middot omiddotmiddotmiddot=ltgt 6

1000

2500

ri1~ 1500J

~ 2000E

obtained at high pressure to that obtained at atmos-pheric pressure and a normalised UTS of 1middot0 indicatesno measurable effect of superimposed pressure onthe UTS The data for the monolithic metalsshown in Figs 10-13 as well as those summar-ised in Fig 14a and b indicate that superimposedpressure generally has a relatively minor effect on theUTS of most monolithic metals though someexceptions are shown Figure 15a and b illustratesthat composite materials often exhibit significantpressure dependent values for the UTS This hasbeen attributed152185189-201 to the pressure inducedsuppression of damage associated with the reinforce-ment and the matrix (eg void initiationgrowthcoalescence) which is covered in more detail in thefollowing sections on fracture behaviour

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 159

Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

A-+

bull -- -

0middot ------ -----()---6 - - - -

-8

iJII

-4-

-8-

---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

-8--- -lt)-

--

1000

5000

4000

C~ 3000~rJ5

2000 l-3~0

o S - - ~ lJS

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

I I I I I Iii I i

- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

3000

2500 -

d )000 f~~ -

~ 1500

~ middot_cmiddot- ~1000 ~_ibullbullbullbullbull~ - - -- - -- --0

s ti

500

12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure llPa

Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

- - -fr-

---]--

----T-

---0--

- - -lS -

------ - --(gt

--+-0-

4340 tempered 3000e 152

4340 tempered 5000e I 52

4340 tempered 7000e 152

01 Tool Steel Hard 152

01 Tool Steel Medium 152

01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

o 2124AI-14SiCw IJlm-UA 152201

bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

-+ Cu-28W 152

- - - -() - - - AI- Al Ni 152-

800

- - - -----------

~z~~~---~-----~bull-----~200

(a)

ts------6---1---------------- ------~

(b)

20

oo 100 WO ~O 400 ~O WO mo WO

Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

05

100

1000

1000

(a)

(b)

800

800600

600400

400

lZ91 19i

200

200Superimposed Hydrostatic Pressure MPa

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot-[H

----- ------0--middot- ----0

------6--- --6- ----------fJ--- --6

-----[S]----- ----[S]

-1-- - - - - - gtJ- - - - - - -Y- - -- - - -I- - - - - - gtJ

- -_~ ~~-~----- ~ _

middotmiddot~~-plusmn~middot~1middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

Superimposed Hydrostatic Pressure MPa

(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

~~ 1500

rJ5~ 1000

500

00

20

1500~~8 10l-o0Z

05

000

categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

References1 T von KARMAN Z Ver dt lng 19115517492 P W BRIDGMAN Proc Am Acad Arts Sci 1911 47 3473 P W BRIDGMAN Philos Mag 1912 24 634 P W BRIDGMAN Proc Am Acad Arts Sci 191449 6275 P W BRIDGMAN Phys Rev 1916 7 215

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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Mechanics Zurich 1926 53 1927 Zurich Orell Fiissli13 P w BRIDG~IAN Phys Rev 1927 29 18814 P W BRIDG~IA Proc Am Acad Arts Sci 192964 3915 P w BRIDG~[A Proc Am Acad Arts Sci 1931 66 25516 P w BRIDG~IA Proc Am Acad Art Sci 1933682717 P w BRIDG~IAN Phys Rev 1935 48 82518 P w BRIDG~[AN J Appl Phys 1937 8 32819 P w BRIDG~IAN Trans AIJvIE 1938 19 92220 P w BRIDG~IAN Jet Technol 1938 5 3221 P w BRIDG~IAN AJech Eng 193961 (2) 10722 P w BRIDG~IAN Pmc Am Acad Arts Sci 1940 74 123 P w BRIDG~IA Proc Am Acad Arts Sci 1940 74 1124 P w BRIDG~IAN Trans ASJvI 1944 32 55325 P w BRIDG~IAN Am Sci 1943 31 126 P w BRIDG~IAN in Colloid chemistry (ed J Alexander) 327

1944 New York Van Nostrand27 P w BRIDG~IAN JVIet Teclmol 1944 11 3228 P w BRIDG~IAN Rev lVIod Ph)s 1945 17 329 P W BRIDG~IAN J Appl Plzys 1946 17 69230 P w BRIDG~IAN J Appl Phys 1946 17 20131 P w BRIDG~IAN J Appl Plzys 1946 1722532 P w BRIDG~IAN J Appl Phys 1947 1824633 P w BRIDG~1AN in Fracturing of metals 240 1948 Cleveland

OH ASM34 P w BRIDG~IAN Research 1949 2 55035 P w BRIDG~IAN Endeavour 1951 106336 P W BRIDG~IAN Studies in large plastic flow and fracture -

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343 c LIU and J J LEWANDOWSKI Unpublished research CaseWestern Reserve University Cleveland OH 1991

344 c LIU G MICHAL and J J LEWANDOWSKI in Residual stressesin composites measurement modeling and effects on thermo-mechanical behavior (ed E V Barrera et al) 1993 DenverCO TMS

345 P F THOMASON Ductile fracture of metals 1990 New YorkPergamon Press

346 J F KNOTT Fundamentals of fracture mechanics 1973London Butterworths

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348 R O RITCHIE and A W THOMPSON Metall Trans A 198516A233

349 F A McCLINTOCK and A S ARGON Mechanical behaviour ofmaterials 1966 Reading MA Addison-Wesley

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Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

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York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

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Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

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397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 147

pressure vessel mantle

7y 6_10_m_m f-pressure vessel liner

servohydraulicactuator bull

argon gas line

a internal load cellb specimen

2 Schematic diagram of gas based high pressure deformation apparatus271273330334

265 268 269 271-273 276-278) References to theeffects of superimposed pressure on creep265281-286have also been provided though this aspect is notcovered in this review

Pressure generation in the oil based systems ofteninvolves compression of the fluid in a pressure vesselvia pressing a plunger in to the bore of a pressurevessel as shown in Fig 1 Pressure is typically moni-tored via the use of a manganin coil pressure gaugethat is exposed to the high pressure environmentManganin coils are used in this case because of thehighly reproducible and linear manner with whichthe resistance of the coil varies with changes inpressure22332 Simple pressurisation experiments canbe conducted with such systems whereby a materialis placed into the pressure vessel and the fluid (ieoil) is compressed to produce a measurable level ofhydrostatic pressure In such simple pressurisationstudies the pressure is subsequently reducedremovedin order to measure the resulting behaviour of thematerial at atmospheric pressure Typically both thepressurisation rate and depressurisation rate aremonitored and kept at a constant low value becauseof the possibility of significant specimen heating (orcooling) during the pressurisation (depressurisation)cycles

Mechanical testing with superimposed hydrostaticpressure has also been conducted on similar devicesto that shown in Fig 1 In these cases the specimenis typically inserted into the load train assemblypresent in the pressure vessel shown in Fig 1 followedby pressurisation of the fluid and the subsequenttension (or compression) testing of the specimen atthe desired level of superimposed hydrostatic pressureIn such tests the high pressure fluid has access to allsurfaces of the specimen It is important to monitorcontinuously (and keep constant) the pressure dur-ing the test in addition to having the capabilityto monitor accurately the load and displacementrequired to deform the specimen under pressure aspointed out elsewhere33o In oil based pressure systemssuch as that shown in Fig 1 the confining (iehydrostatic) pressure is kept constant via either using

an intensifier or retracting the bottom hydraulicpiston while inserting the top plunger In such testingthe use of external load cells (ie positioned on theload train but outside of the pressure vessel) mayproduce erroneous data for the load required todeform the specimen because of the variable amountof seal friction which results during the generation ofpressure in the chamber In an attempt to determinethe load on the specimen inside the vessel moreaccurately pressure compensated load cells consistingof a measuring load cell and a compensating loadcell were developed330333 as shown schematicallyin Fig 1 Displacement andor strain measurementin such studies has typically relied on monitor-ing piston displacement though more recentstudies103 155-157161-163189190192-195197have utilisedpressure compensated strain gauges affixed to thespecimen surfaces In some studies195197213the press-ure vessel was fitted with machined cross-bores andtransparent quartz windows as shown in Fig 1 whichenabled in situ monitoring of deformation and thedevelopment of necks under pressure

Gas based systems like that shown schematicallyin Fig 2 typically utilise a pressure intensifier togenerate pressure that is contained within a multi-walled pressure vessel where the volume of gas pre-sent at high pressure in the vessel is kept as low aspossible because of the danger associated with thestored energy Such systems often utilise many of thesame types of diagnostic techniques as that describedabove though direct visual monitoring of the speci-men during deformation has not been conductedbecause of the inherently higher danger associatedwith gas based systems Pressure fluctuations duringmechanical testing in gas based systems are typicallymuch less than those of the oil based systems wherethe pressure generation techniquedevice is directlylinked to the piston which controls displacement ofthe specimen

Tables 1 and 2 summarise many of the variousinvestigators that have utilised high pressure testingto evaluate the mechanical behaviour of materialsTable 1 summarises the maximum pressure utilised

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148 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 149

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150 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Table 2 Summary of investigations on effects of hydrostatic pressure on mechanical behaviour ofinorganic materials - categorised by class of material

Pressu re range

Materials Researcher(s) Failure mode P MPa Measured properties Note

0-27 (UTS) Ef

Ef

Ef

0-15 (UTS) Ef void fraction0-19 (UTS) Ef void fraction

PrepressurisedprestrainedTemperature upto 600aC

Prepressurised

Prepressurisedprestrained

Interrupted testInterrupted test

Prepressurised

Prepressu rised

Prepressu rised

PrestrainedPrepressurised

Interrupted test

Prepressu rised

ay af poundf

ay

ay af EI

ay UTS 8f

Ef

(Iy af poundf

ay af EI

Ef

ay Ef EI n K1c

EI

Ef

Ef

qEf

dadn versus ~Kaf Ef

ay UTS Ef

(Iy UTS qay Ef

(Iy Ef voids quantification

ay af Ef

Ef

ay UTS nEf voids quantification(Iy af qay

ay

dadn versus ~Kay UTS Ef

ay

ay

ay (If Ef

ay UTS Ef

ay UTS Ef

Ef

ay EIEf

ay Ef

Ef

J

CRSS

0-58

0-12

0-270-12

0-7S

0-26

030-110-08

0-330-170-200-08

0-120-110-1S01-020-070-36

OS

0-103

01-500

01-3060

01-290001-S0001-140001-50002000

01-250001-31001000

01-600

01-6900-48001-60001-600

01-20001-296001-35001-80001-900

01-300

01-60001-52001-30001-62001-3501-92001-69001-69001-300

01-110001-60001-7

01-110001-S0001-69001-345100001-2250

01-70001-90001-345150001-69050017201-210001-126001-110017201-110001-110001-3501-69001-110001-110017201-69001-970

Cleavage

Cleavage

MVCshear

MVCshear

MVCshearMVCshear

ShearMVC

Intergranular

MVC

MVCshearMVCshear

MVCshear

MVCdelamMVCshear

MVCshear

MVCshear

MVCshear

Nishihara et al114

French and Weinrich89

Pugh and Green 123

Vajima et al149

Pugh and Green 123

Plumbridge et af121

HU93

ZOk152

ZOk152

Lewandowski etal189190

Liu andLewa ndowski103 195

Korbel et al99

Auger and Francois5051

Franklin et al84

Bridgman36

Ball et al53

Bullen et al64

Mellor and Wronski108

French andWeinrich88141

Vajima et al149

Pugh and Green 123

French and Weinrich85

Weinrich andFrench85141

Omura119

Bridgman36

ZOk152

Vajima et al149

Vajima et al149

Bridgman36

Dobromyslov et af79

Galli and Gibbs90

Kuvaldin et af100

Mellor and Wronski108

Spitzig 135

Vajima and Ishii147148

Vajima et al149

Ohmori et al118

Bullen et al65

Davidson andAnsell7576

Vajima et af149

Itoh et al95

Ohmori et al118

Worthington 144

Pugh and Green 123

Wagner et al140

Johnson et al97

Davidson et af74

McCann et al106

Brownrigg et al63

Johnson et af97

Spitzig et al133

Spitzig et al133

Plumbridge et al121

ZOk152

Spitzig et al134

Spitzig et al134

Johnson et al97

Zok and Embury152153

ZOk152

MoMoMoMoMo

7075AI-T47075AI-T6517075AI

Cu alloysPure

PureERCH CuLeaded brassa-brass a-fJ brass

70-30 40-60 brassy-brassCu-002BiCu-(15-40)ZnCu-(45-97)Ge

Ni alloyPure

bcc metalsCrCrCr

Mo

Fe-(O02-049)CMild steel (OOSC)Mild steel (O14C)Fe-3SiCast ironsSpheroidised cast iron101S steel1045 steel1045 steel1045 steel (spheroidised)4130 steel4310 steel4330 steel4360 steel4340 steelMaraging steelHV SO steelHV 130170180 steels01 tool steelTi-V steel

AI alloysPurePurePureAI-1 Si-07Mg-04MnAI-Cu-Mg-Si61S AI-T42014AI-T6AE2124AI-UAOAMB85-UAOA

6061AI-UAOA

Metals

Ferrous alloysSingle crystal FePure FePure FePure FeArmco FeFe-(0004-11)C

Mo Robbins andWronski131132

Cleavage 01-500

CRSS critical resolved shear stress delam delamination dadn crack propagation rate EI elongation HV Vickers hardness J J-integral MVC microvoidcoalescence UTS ultimate tensile strength

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 151

Table 2 (cant)

Pressure range

Materials Researcher(s) Failure mode P MPa Pj(fy Measured properties Note

Metalsbee metalsNb Bridgman36 01-2850 (ff qTa Bridgman36 01-2850 (ff [f

Ta Nishihara et al114 01-500 ayUTS rof Temperature upto 600C

Ta Robbins and Wronski131 1500 (fy Prepressu rised0-500

W Bridgman36 01-2840 af lofW Das and Radcliffe73 01-1100 0-15 (ff af lofW Daga71 01-1100 0-20 ay (ff qW Davidson et al74 CleavageMVCjshear 01-1600 qW Mellor and Wronski108 2800 (fy af EI Prepressu rised

prestrainedhcp metalsBe (PM) Aladag45 Intergranularj 01-980 af [f

Aldag et al46 transgranularBe (PM) Andrews and 01-2700 Prepressurised

Radcliffe49Be (ingot) Aladag45 Transgranular 01-980 0-38 (fy af [f

Aldag et al46

Be (castrolled) Bedere et al55 Intergranularj 01-1500 0-122 (ly af [f

transgranular shearCd Nakajima et al111 01-600 ayCo Davidson et al74 CleavagejMVCjshear 01-2350 f~Mg Davidson et aJ74 MVCjshear 01-1800 4Mg Pugh and Green 123 01-460 [fAZ91 (PM) Lahaie et al101 Intergranularshear 01-690 0-22 (fy ltofAZ91-T4jT6 Lewandowski et al193 01-380 af (f

Zn Davidson et al74 Brittlejplastic rupture qZn Pugh and Green 123 Cleavageplastic 01-138 ay q

ruptureZn-41AI Pugh and Green 123 01-410 ltofTi-7 AI-2Nb-1Ta (x) Johnson et al97 172 02 ay af lt1 Prepressu risedTi-6AI-4V (ajm Johnson et al97 172 02 (fy (ff Gf Prepressu risedTi-13V-l1 Cr-3AI (x) Johnson et al97 172 0middot2 ay af q Prepressurised

Metal matrix composites

AI matrix2014-20SiCp-T6jAE ZOk152 MVCshear 01-980 0-24 ay UTS Gf

2124-14SiCw-UAjOA ZOk152 MVCshear 01-690 0-20 ay UTS l12014-20SiCp-T6jAE Mahon et al198 MVCjshear 01-980 0-24 ay UTS l12124-14SiCw-UAjOA Vasudevan et al201 MVCjshear 01-690 0-20 ay UTS [f

MB85-15SiCp-UAjOA Lewandowski MVC 01-300 0-08 (ly af (fet al189190

M B85-15SiCp-UAjOA Liu 195 MVC 01-300 0-08 ay (ff q6061AI-15AI203-UAjOA Liu et al194195197 MVC 01-300 0-11 ay af q Damage

quantification6090AI-25AI203-SAjT6 Lewandowski et al193 MVC 01-400 GfMB78-15SiCp-UAjOA Singh and MVC 01-500 q Damage

Lewandowski199 quantificationA356-1 Oj20SiCp- T6 Embury et al184 MVC 01-850 q Damage

quantificationAI-AI3Ni Zok 152 MVC 01-690 0-45 ay UTS lt1

Mg matrixAZ91-20SiCp-T4 Lewandowski et al193 01-350 0-12 GfAZ91-19SiCp15 llm-T6 Lewandowski et al193 MVC 01-440 0-14 ay UTS af [f Damage

quantificationAZ91-20SiCp52 llm-T6 Lewandowski et al193 MVC 01-490 0-19 ay UTS af [f Damage

quantificationCu matrixCu-28W Zok152 MVC 01-690 UTSq

IntermetallicsNiAI Margevicius and Transgranularj 01-1400 0-140 (ly (ff Gf wj

Lewandowski155161163 inte rg ra nul ar PrepressurisedNiAI Weaver et al166167 Prepressu risedNi3AI Zok et al152170 Intergranular 01-965 af GfAI3Ti Witczak and Varin 169 2000 ay af lof HV PrepressurisedAmorphous metalsPd Cu Si Davis and Kavesh323 Shear 01-690 0-047 af EfZr Ti Ni Cu Be Lewandowski et al324 Shear 01-650 0-035 af Ff

CeramicsAI203 Bridgman36 2350-2960 afB203 Bridgman3637 2350-2960 af Gf density changeLiF Hanafee and 01-1300 Dislocation velocity

Radcliffe 176MgO Weaver and Brittlejshear 01-1000 ay af Ff

Paterson 180181NaCI Bridgman36 2350-2960 af [f

CRSS critical resolved shear stress delam delamination dajdn crack propagation rate EI elongation HV Vickers hardness J J-integral MVC microvoidcoalescence UTS ultimate tensile strength

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152 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

and any pressure variation reported during the testin addition to the load and strain measurementtechniques reported by the various investigators onthe materials listed Table 2 provides a similar list ofinvestigations organised by the type of material (egmetal intermetallic composite) tested as well as bythe crystal structure (eg bcc fcc hcp) of the metalsunder investigation Included in Table 2 are thespecific properties measured by each of the investi-gators and any comments related to the failure modespresent References to the works in Tables 1 and 2are provided while the specific data summariesappear in subsequent figures In most of the studieswhere testing is conducted with superimposed hydro-static pressure the specimens have been coated orjacketed274 with some impervious membrane (egpolymer Cu shrink fit tubing etc) in order to preventingress of the pressure medium into any surfacecracks porosity etc274 The membrane utilised istypically very thin and does not contribute signifi-cantly to the load bearing area of the specimenFurthermore pressurisation of specimens shieldedwith such membranes in and of itself has not pro-duced changes to the subsequent flow stress obtainedat atmospheric pressure

1

-2-1

o~ 1cr

2

3 Yield surface plotted in principal stress spacefor fully dense isotropic and homogeneousmaterial335336

(2)

(4)

(5)

ka = 511 + 512 + S13

kc = 2S13 + 533

shear stresses developed owing to the differences incompressibility between the matrix and the secondphase128 The maximum shear stress [max at thematrixsecond phase interface has been separatelyestimated by Das and Radcliffe73 and Ashby et al337

for a spherical particle and is given by

3Gm ( Km -Kp )[max = K 3K + 4G pm p m

where Gm is the shear modulus of the matrix Km

and K the bulk moduli of the matrix and the sec-ond phase respectively and P the applied hydro-static pressure Dislocations are generated when[max reaches the nucleation stress for dislocationgeneration which can be theoretically predicted ordetermined experimen tally338

Another manner in which shear stresses are gener-ated in polycrystalline materials through the simpleapplication of hydrostatic pressure is through theanisotropy of elastic constants91128 Crystals of allsystems except the cubic system can change shapewhen subjected to hydrostatic pressure cubic crystalshave isotropic bulk moduli The volume compress-ibility which is the inverse of the bulk modulus isthe pressure induced change in volume of a crystalnormalised to its original volume and the linearcompressibility k is the amount of pressure inducedlength change in a straight line normalised to itsoriginal length For the cubic system k is independentof orientation and is related to the elastic compliance5ij through

k = 511 + S12 bull bull bullbull bull (3)For the trigonal hexagonal and tetragonal systemstwo constants are required the value in the a directionka and the value in the c direction kc These compress-ibilities are related to the elastic compliance 5ij by

Effects of superimposed pressure onstress state in cylindrical specimensConditions present before necking incylindrical specimensPlastic deformation in metallic systems tested at lowhomologous temperatures primarily occurs via dislo-cation generation andor movement via shear stressesoften referred to as conservative motion or glidePlastic deformation under such conditions occurswhen the effective stress (j equals the yield strengthin tension (Jy where the effective stress is given as

- 1 ( )2 ( )2 ( )2] 120=0[(J1-(J2 + 02-(J3 + (J3-(J1

(1)and (Jb (J2 and (J3 represent the principal stressesThe application of a purely hydrostatic stress (ie(J1 = 02 = (J3) produces no shear stress in a homo-geneous and isotropic material as shown by the 3-Dyield surface plotted in stress space in Fig 3 Ahydrostatic stress is represented as the axis of thecylinder in Fig 3 and since such stresses never touchthe yield surface there should be no effect ofpressurisationpressure soaking on the subsequentflow behaviour when uniaxial testing is conducted atatmospheric pressure Pressurisation in this casedenotes the simple application of hydrostatic pressureto a material and its subsequent removal Thereshould similarly be little effect of superimposed press-ure on yielding when testing is conducted on acylindrical specimen in the presence of a confining(ie hydrostatic) pressure as the stress state up to theultimate tensile stress (UTS) (ie before necking) insuch specimens consists of the uniaxial stress plusany superimposed hydrostatic pressure

However simple pressurisation can serve as ameans for generating dislocations in a materialaround inclusions and other defects as there are local

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 153

1

4 Yield surface plotted in principal stress spacefor material containing void fraction of a 0057and b 0180 (Ref 336)

1

1

a~l 05cr

o~ta

-05

-1

-1

(a)

(b)

The linear compressibility in any other direction kris given by

kr = ka + (ke - ka)r2 (6)

where r is the direction cosine with subject to thec axis

If non-cubic metals can change shape because ofpressurisation then a random aggregate of manycrystals when subjected to unit hydrostatic pressurewill develop shear stresses across grain boundaries Itis this shear stress which produces dislocation gener-ation in anisotropic materials

The degree of anisotropy in these non-cubic systemsis given in terms of the ratio keka The anisotropy ofa number of hexagonal metals is given in Table 3Those metals with a high degree of anisotropy Cdand Zn have been shown91339 to require only modestlevels of pressure ( 300 MPa) to induce plastic strainin the grains while metals with ratios close to one(where a cubic metal equals 10) Zr and Mg requiredthe highest pressures ( 2middot6 GPa) to produce onlytrace amounts of plastic deformation Although TEManalyses have confirmed the presence of pressureinduced dislocations around inclusions in less pureFe and Fe-C alloys containing inclusions65139 highpurity cubic metals such as Cu AI Fe and Ni haveshown no such plastic deformation after pressuris-ation to levels up to 1 GPa (Refs 109 339)

Porous materials consisting of either interconnectedor isolated pores are also highly pressure sensitive340provided the pressure medium is shielded from thespecimen to prevent ingress of the pressure medium(ie gas liquid) into the pores The 3-D yield loci forsuch materials are distinctly different from that shownin Fig 3 for homogeneous and isotropic materialsShown in Fig 4 are 3-D yield loci for porous materialscontaining increasing levels of porosity335336341342It is clear that the application of a hydrostatic pressureof sufficient magnitude in these cases can touch theyield surface and thereby produce plastic flowExamples of such effects are provided in works onporous Fe (Refs 62 137)

where Oflow is the flow stress a the minimum specimenradius R the radius of curvature at the neck or notchand rn the distance from the centre along the planeof the neck

Since the notchneck geometry will often changewith additional deformation the level of triaxialtensile stress resulting from deformation of such

International Materials Reviews 1998 Vol 43 NO4

mens) when subsequently tested in tension also experi-ence triaxial tensile stresses in the neckednotchedregion In this case the major difference between thenecked region which evolved during deformation andthat simulated by prenotching a pristine (ie non-deformed) specimen relates to the differences indeformation history (and any damage) present in thenecked region as compared to the notched regionBridgman provided an estimate of the additionalhydrostatic tension OT in the plane of a neck ornotch2436 as

Conditions present past necking incylindrical specimensOnce a neck begins to form in a cylindrical tensilespecimen tested at atmospheric pressure triaxialtensile stresses develop in the necked region Boththe magnitude and location of such triaxial stressesvary with location in the neck which develops withadditional deformation Prenecked (eg notched speci-

Table 3 Linear compressibility and anisotropyfactors for some non-cubic materials(Refs 128 339)

Lattice ratioLinear compressibility MPa

Metal cia c axis ke a axis ka Ratio keka

Cadmium 18856 1890 x 106 217 X 106 870Zinc 18564 1341 x 106 201 X 106 670Bismuth 26095 1645 x 106 684 X 106 240Magnesium 16235 1016 x 106 1016 X 106 1middot00Zirconium 1middot5931 380 x 106 3middot80 X 106 1middot00Titanium 15870 270 x 106 270 X 106 100Beryllium 15684 227 x 106 291 X 106 078

(a 12 )

OT = Oflow In 1 + 2R - 2a~ (7)

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154 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Superimposed Hydrostatic Pressure MPa

4340 tenlpered 3000C 152

4340 tempered (eQ 5000C 152

4340 tempered 7000C 152

o 4310-Lower Yield 133

bullbull 4330-Lower Yield 113

6 01 Tool Steel Hard 152

6 01 Tool Steel Mediunl 152

6 01 Tool Steel Soft 152

[S ri-V Steel 9500C FRT 152

fpound Ti-V Steel 700degC FRT 15~

bull 7075AI-T651(TR) 5051

bull 7075AI-T65 I(WR) 5051

T 7075AI-T65I (RW) 5051

() 201411 1(21)

EE BY -80 1ower Yield 134

bull Maraging-Unaged (Ten) 134

bull Maraging-Unaged (Comp) ]34

bull Maraging-Aged (Ten) 134

bull1200

(a)

bullbull

1000

EB

[SJ

800600400200

bull bull bull bullbullbullII bullbull JI bullbull Q bullbull bull

~ 6III II II bull

j 6 i i6

o

20

o

=~~ 15Q)~~

rJ)

0

~ 10~

e~ 05Z

~~ 1500

2000

=~eJ)

~ 1000~~

rJ)

e-Q)

~

00(b)

(gt 2124J() () I

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure

5 Effect of pressure on yield strength of various bee and fcc metallic alloys

specimens will vary past necking in the cylindricalspecimen Thus while the level of superimposedhydrostatic pressure has been kept relatively constantin many of the studies listed in Tables 1 and 2 thetriaxial stresses present in the neck during tests withsuperimposed pressure will depend on a variety offactors including the neck geometry level of superim-posed pressure and the flow stress of the materialIt is important to note that some studies investigat-ing the effects of superimposed pressure on tensiontests have been conducted under conditions suchthat compressive triaxial stresses were present in thenecked region In these cases the levels of superim-posed pressure were high enough to overcome thetriaxial tensile stresses which developed in the evolv-ing neck Thus the ability to monitor visually thedevelopment of the neck during tests with superim-posed pressure as described above or conductinginterrupted tests where the neck can be physicallymeasured outside of the high pressure environmenthas some merits858689103197213

Effects of superimposed pressure onflow behaviourEffects of superimposed pressure onyield stressFigures 5-8 summarise published data on the effectsof pressurisationpressure soaking as well as tensiletesting at different levels of superimposed hydrostaticpressure on the yield strength typically reported asthe 0middot2 offset yield strength In the former tests theyield strength was measured at atmospheric pressureafter pressurisation while the measurements of yieldstress in the latter cases occurred during tensile testsconducted with superimposed hydrostatic pressureThe pressure medium utilised in the studies summar-ised was either an oil medium or Ar gas and wasconfirmed to be hydrostatic Figure 5 summarisesdata obtained on a variety of steels and aluminiumalloys while Fig 6 shows similar data obtained on avariety of single phase metals possessing a bcc crystalstructure Figure 7 is a plot of the same type of

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 155

___bull __ Ar111co Iron 65

5b 6b 7b and 8b are plots of the ratio of the yieldstrength obtained at pressure (or after pressure soak-ing) to that of the control material (ie no pressuresoaking) in the manner utilised by a number ofinvestigators henceforth this is called the normalisedyield strength Pressure independent yielding is rep-resented by the horizontal line at 1middot0 for the normal-ised yield strength in Figs 5b-8b It is clear fromFig 5a that a number of conventional structuralmetallic alloys exhibit nominally pressure independ-ent yielding behaviour as predicted by equation (1)Slight positive deviations for monolithic materials (ienormalised yield strengthgt 1 in Fig 5b) have beenexplained as in part due to the pressure depend-ence of the shear modulus which though modestis non-zero for various metallic materials136Models313314 have been developed to predict suchpressure dependent yielding in metallic materials andmetallic glasses321-323 and a few studies have invokedsuch models to explain such pressure dependence ofthe yield stress136 It should be noted that there havebeen observations of materials which exhibit muchgreater positive deviations than those of the monolithicmetals summarised in Fig 5a and b For example ithas been clearly shown that superimposed pressuresignificantly inhibits dislocation mobility in LiFthereby elevating the flow stress above that obtainedat atmospheric pressure176

It is also clear that some of the monolithic metalsshown in Fig 5a and b as well as a variety of bccmetals (cf Fig 6a and b) and certain chemistries ofthe intermetallic NiAI shown in Fig7a and b ex-hibit a significant decrease in the yield strength afterpressure soaking or during tests conducted withsuperimposed pressure In these cases the materialstypically exhibited a yield point and Liiders exten-sion before pressure soaking or testing with superim-posed pressure Pressurisation (andor testing withpressure) was shown to remove the yield pointand Liiders strain and thereby reduce the yieldstrength155157159161162166167as illustrated for castextruded NiAI in Fig 7c As shown in Figs 6a andband 7a and b large reductions in yield strengthwere obtained in Fe (Refs 65 147) Cr (Refs 59 6466 72) and commercially pure NiAI (Refs 155 157161-163) that had been cast and extruded ExtensiveTEM analyses in these cases revealed that pressureinduced dislocation generation occurred at non-metallic inclusions and other inhomogeneities in thesematerials6465155157158161an example of which isshown in Fig 7d (Ref 157) The generation of thesemobile pressure induced dislocations thereby reducedthe yield strength while subsequent thermal agingstudies conducted for sufficient time-temperaturecombinations at atmospheric pressure enabled relock-ing of the dislocations by interstitial impurities (egC) and a return of the yield point and Liidersstrain6465107147166as illustrated for NiAI in Fig7c(Ref 159) Similar studies166167 conducted on highpurity NiAI failed to reveal a yield point and anysubsequent effect of pressurisation on the yield stressas shown in Fig 7a and b consistent with sucharguments Pressurisation of the largest grained Fein Fig 6a and b (Ref 147) to increasingly higherpressures eventually produced excessive generation

International Materials Reviews 1998 Vol 43 NO4

1200

(a)

(b)

---)

1000800600

~_-----1-~ - --

400200

- - Chromium 64

bull - Iodide Chromium 72

Superimposed Hydrostatic Pressure MPa

bull ~ ~- Y- -y_~~~ - - -9

-------

cOil 15cQJ

000 10~~5 050Z

000

800

eo 700~~ 600pound 500eiJcCJ 400V)

0 300~~ 200

100o

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

20

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

6 Effeet of pressure on yield strength of variousbee metals GS grain size

--0 Fc GS=11Jlnl 147

-0 Fe GS=14Jlm 147

-[S- Fe GS=19Jlm 147

-83- - Fe GS=30Jlm 147

-- - Fe GS=450~lIn 147

6 - - PM T 72- ungsten

-pound --Arc-Melted Tunsten 72

information for the intermetallic NiAI which possessesa B2 (ie bcc derivative) crystal structure while Fig 8is a plot of data from more recent work on compositesbased on either aluminium or magnesium alloymatrixes The data reported for the control materials(ie no pressure soaking) occur on the ordinate at0middot1 MPa (ie atmospheric pressure) Figures 5a 6a7a and 8a summarise the reported values for theyield strength obtained either during tension testswith superimposed pressure or after pressure soakingat the levels of hydrostatic pressure indicated Figures

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156 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullNill Cast and extruded 161

-[S)- - CP-NiAI Prepressurised 166

-EB - - - HP NAlP d 166- 1 repressunse

- -- - - - NiAI-NPrepressurised 166

50

300

(a)

1500

EB

(b)

middotmiddotlSI

__

middotEB

-bullbull-

bull

1000

-----------

1

500

_------------ --- -_---

Superimposed Hydrostatic Pressure MPa

100

50

20

00

o

c~ 15QJl-rj~ 10~8~ 05Z

oo 500 1000 1500

Superimposed Hydrostatic Pressure MPa

el~~ 200

250

o annealedp ~a~~a p ~a~~a p ~~~aT = 200degC 2h T = 400degC 2h

Strain

(c)d

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure c stress-strain curvesof polycrystalline NiAI tested in tension after annealing at 82JOC for 2 h pressurised to 14 GPa and tested at atmospheric pressure and afteraging pressurised specimens at either 200degC or 400degC for 2 h (Ref 159) (arrows show proportional limit) d dislocations being punched from Zrinclusion in NiAI pressurised to 1middot4 GPa (Refs 156 157 160 161)

7 Effect of pressure on yield strength of NiAI

of dislocations and a slight increase in the yieldstrength because of work hardening Little effect ofpressurisation was 0bserved on higher strengthPowder metallurgy produced NiAI (cf Fig7a

International Materials Reviews 1998 Vol 43 No4

and b)166 or W as well as arc-melted W (cf Fig6aand b) 72 in part due to the higher strengths of thematerials tested and the limited range of pressuresutilised

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 157

500

600(a)

Effects of pressure on work hardeningexponent nThe effects of testing with superimposed pressureon the work hardening exponent n have beeninfrequently studied Figure 9a and b illustrates theexperimentally measured effect of superimposed press-ure on n for a high strength aluminium alloy(7075- T651) tested in different orientations withrespect to the rolling direction Testing was conductedwith superimposed pressure on either uniaxial tensionspecimens or plane strain tension specimens andgenerally revealed an increase in n with increasingpressure The authors5051 indicated that such obser-vations could be related to the amount of secondphase particles which could punch out dislocationloops because of their smaller compressibility in amanner analogous to that described above for thecomposite materials

yield stress apparently arises because of pressureinduced dislocation generation around the reinforce-ment which increases significantly the local dislo-cation density thereby providing local hardening anda higher yield strength192195196 Transmission elec-tron microscope studies have confirmed that suchevents can occur provided the pressurisation is con-ducted at a large enough pressure to generate shearstresses of sufficient magnitude near the reinforce-ment192 Testing with superimposed pressure has alsobeen shown to inhibit the accumulation of damage(eg void initiation and growth) in such materials Asthe accumulation of damage reduces the load bearingarea and instantaneous modulus in such compositesand thereby reduces the strain hardening rate press-ure induced damage suppression has been proposedas also contributing to the elevated flow stressesobtained during tests conducted with superimposedpressure192196201 This point is further discussedbelow when summarising the effects of confiningpressure on the UTS In addition recent work hasalso shown that the level of residual stress in thematrix and reinforcement can be changed via pressur-isation343344 Finally various models315-320 have indi-cated that the presence of the non-deformingreinforcement particles provides constrained flow andenhances the flow stress of the matrix The super-position of pressure during tension testing shouldcounteract this effect as illustrated in a fewpapers318-320

15001000

== 0---

~ - - - ---= = = t0- -- - -

(b)

500Superimposed Hydrostatic Pressure MPa

oo

20

EZ 05-

- --6--- 2014AI-20SiCp 13 Jlm-AE 152201

-J - - 2014AI-20SiCp 13 Jlm-T6 152201

-1- - - 2124AI-14SiCw 1 Jlrn-UA 152201

-T---- 2124AI-14SiCw 1 ~m-OA 152201

-X - AI-AI Ni l~m 1523

0-- IIOOAJ-IOAI)O_~ 193

ltgt 193- -- 1100AI-15Al)0 -

- -0- - - 6061AI-15AJ 0 13lrn-UA 1952 3

-- -0- -- 6061AI-15AI 0 (13lm-OA 1952 3

- - -[SJ- - - 6061AI-15At) 0 13~ln-UA 185_ 3

- - -EB- - - 6090AI-25SiCp-SA 193

- - -- - - 6090AI-25SiCp-T6 193

-0- AZ91-19SiCp 15~lTn-T6 193

-e- AZ91-20SiCp52-lIn-T6 J93

c ~~~1-~ 200l x~ -X- X- y

100

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

8 Effect of pressure on yield strength ofdiscontinuously reinforced metal matrixcomposites

The largest changes in the yield strength obtainedeither after pressurisation or during tests with super-imposed pressure have been exhibited by compositematerials as shown in Fig 8a and b (Refs 152 185191-196 198 200 201) One source of the enhanced

Superimposed Hydrostatic Pressure MPa

00o 500 1000 1500 Effects of pressure on UTS

The experimental data for the UTS obtained viatension testing with a range of superimposed pressuresare provided for both monolithic metals as well ascomposites in Figs 10-15 As indicated above thestress state at the UTS (ie before necking) in suchspecimens consists of the uniaxial stress plus anysuperimposed hydrostatic pressure Data obtainedfrom some of Bridgmans original works are providedin Figs 10-13 for a variety of ferrous based systemsheat treated to different strength levels and micro-structures Figure 14a summarises similar data for avariety of other ferrous and non-ferrous structuralmaterials Figure 14b provides the ratio of the UTS

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158 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-6- _ TR uniaxialmiddotmiddotAmiddot TR plane strain-0 --- TW uniaxial

----e TW plane strain-0 - WRuniaxialbull - WRplanc strain

- --0 RW uniaxial- -+- - RW plane strain

-fSJ- Fe-034C-O75Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-045C-O83Mn-OO l6P-O035S-O19Si (as-received)

o normalised l650degF---0 annealed fine-grained- -6- annealed coarse-grained

- - - - - brine-quenchedtenlpered 600degF- - -+- - - brine-quenchedtempered 600degF-- -bull- - -- brine-quenchedtempered 900degF

015 3000

3000

middot11bull

1500 2000 25001000500Superimposed Hydrostatic Pressure MPa

o-- -0--

-6---e----+- -

--SJ-- Fe-O68C-O 7lMn-OO l3P-O025S-O19Si (as-received)

----0 --- Fe-O9C-O47Mn-O015P-O036S-OllSi (as-received)normalised 1650degFannealed fine-grainedannealed coarse-grainedbrine-quenchedspherodisedbrine-quenchedtempered 600degFbrine-quenchedtenlpered 900degF

bullbullbull

oo

2500

500

ce~E 1500rrJ~J 1000

10 Effect of pressure on UTS of various steelstested by Bridgman36

600

(a)

500 600

500

IImiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

middot0-middot -0

400

400

0

300

300

200

200

(b)

100

100Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

bullbull - A R bullbull

~ bull ~

000o

= 200Q)

=oc0lt

~ 150~=2

Q)C

100tt==~ 050eoZ 000

o

a n v hydrostatic pressure b normalised n v superimposedhydrostatic pressure

9 Effect of pressure on strain hardening exponentn of 7075AI- T651 (Refs 50 51)

3000

11 Effect of pressure on UTS of various steelstested by Bridgman36

Superimposed Hydrostatic Pressure MPa

500o

o -0

1500 2000 2500 30001000500

bullbull middot11II bull

~o Q ~omiddot omiddot

6 middot0middot omiddotmiddotmiddot=ltgt 6

1000

2500

ri1~ 1500J

~ 2000E

obtained at high pressure to that obtained at atmos-pheric pressure and a normalised UTS of 1middot0 indicatesno measurable effect of superimposed pressure onthe UTS The data for the monolithic metalsshown in Figs 10-13 as well as those summar-ised in Fig 14a and b indicate that superimposedpressure generally has a relatively minor effect on theUTS of most monolithic metals though someexceptions are shown Figure 15a and b illustratesthat composite materials often exhibit significantpressure dependent values for the UTS This hasbeen attributed152185189-201 to the pressure inducedsuppression of damage associated with the reinforce-ment and the matrix (eg void initiationgrowthcoalescence) which is covered in more detail in thefollowing sections on fracture behaviour

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 159

Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

A-+

bull -- -

0middot ------ -----()---6 - - - -

-8

iJII

-4-

-8-

---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

-8--- -lt)-

--

1000

5000

4000

C~ 3000~rJ5

2000 l-3~0

o S - - ~ lJS

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

I I I I I Iii I i

- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

3000

2500 -

d )000 f~~ -

~ 1500

~ middot_cmiddot- ~1000 ~_ibullbullbullbullbull~ - - -- - -- --0

s ti

500

12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure llPa

Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

- - -fr-

---]--

----T-

---0--

- - -lS -

------ - --(gt

--+-0-

4340 tempered 3000e 152

4340 tempered 5000e I 52

4340 tempered 7000e 152

01 Tool Steel Hard 152

01 Tool Steel Medium 152

01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

o 2124AI-14SiCw IJlm-UA 152201

bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

-+ Cu-28W 152

- - - -() - - - AI- Al Ni 152-

800

- - - -----------

~z~~~---~-----~bull-----~200

(a)

ts------6---1---------------- ------~

(b)

20

oo 100 WO ~O 400 ~O WO mo WO

Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

05

100

1000

1000

(a)

(b)

800

800600

600400

400

lZ91 19i

200

200Superimposed Hydrostatic Pressure MPa

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot-[H

----- ------0--middot- ----0

------6--- --6- ----------fJ--- --6

-----[S]----- ----[S]

-1-- - - - - - gtJ- - - - - - -Y- - -- - - -I- - - - - - gtJ

- -_~ ~~-~----- ~ _

middotmiddot~~-plusmn~middot~1middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

Superimposed Hydrostatic Pressure MPa

(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

~~ 1500

rJ5~ 1000

500

00

20

1500~~8 10l-o0Z

05

000

categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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62 S B BINER and W A SPITZIG in Modeling of the deformationof crystalline solids (ed T C Lowe et al) 545 1991Warrendale PA TMS

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356 A N STROH Adv Phys 1957 6418357 A N STROH Phios Mag 1958 3 597358 1 FREIDEL Dislocations 1964 New York Pergamon Press359 1 F KNOTT and A H COTTRELL J Iron Steel Inst 1963

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Moscow USSR365 1 1 LEWANDOWSKI and A W THOMPSON Metall Trans 1986

17A 1769366 J J LEWANDOWSKI and A W THOMPSON Acta Metall 1987

35 1453367 A SAMANT and 1 J LEWANDOWSKI Metall Mater Trans A

1997 28A 389368 D TEIRLINCK F ZOK J D EMBURY and M F ASHBY Acta

Metall 1988 36 1213369 D TEIRLINCK M F ASHBY and J D EMBURY in Advances in

fracture research - ICF 6 New Delhi India Dec 1984 105New York Pergamon Press

370 w M GARRISON Jr and N R MOODY J Phys Chem Solids1987 48 1035

371 A W THOMPSON Metall Trans A 1987 18A 1877372 L M BROWN and J D EMBURY in Proc 3rd Int Conf on

Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

374 s H GOOD and L M BROWN Acta Metall 197927 1375 L M BROWN and w M STOBBS Phios Mag 197634 351376 P F THOMASON Ductile fracture of metals 94 1990 New

York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

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408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

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411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

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Rev 1993 38 193

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148 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 149

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150 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Table 2 Summary of investigations on effects of hydrostatic pressure on mechanical behaviour ofinorganic materials - categorised by class of material

Pressu re range

Materials Researcher(s) Failure mode P MPa Measured properties Note

0-27 (UTS) Ef

Ef

Ef

0-15 (UTS) Ef void fraction0-19 (UTS) Ef void fraction

PrepressurisedprestrainedTemperature upto 600aC

Prepressurised

Prepressurisedprestrained

Interrupted testInterrupted test

Prepressurised

Prepressu rised

Prepressu rised

PrestrainedPrepressurised

Interrupted test

Prepressu rised

ay af poundf

ay

ay af EI

ay UTS 8f

Ef

(Iy af poundf

ay af EI

Ef

ay Ef EI n K1c

EI

Ef

Ef

qEf

dadn versus ~Kaf Ef

ay UTS Ef

(Iy UTS qay Ef

(Iy Ef voids quantification

ay af Ef

Ef

ay UTS nEf voids quantification(Iy af qay

ay

dadn versus ~Kay UTS Ef

ay

ay

ay (If Ef

ay UTS Ef

ay UTS Ef

Ef

ay EIEf

ay Ef

Ef

J

CRSS

0-58

0-12

0-270-12

0-7S

0-26

030-110-08

0-330-170-200-08

0-120-110-1S01-020-070-36

OS

0-103

01-500

01-3060

01-290001-S0001-140001-50002000

01-250001-31001000

01-600

01-6900-48001-60001-600

01-20001-296001-35001-80001-900

01-300

01-60001-52001-30001-62001-3501-92001-69001-69001-300

01-110001-60001-7

01-110001-S0001-69001-345100001-2250

01-70001-90001-345150001-69050017201-210001-126001-110017201-110001-110001-3501-69001-110001-110017201-69001-970

Cleavage

Cleavage

MVCshear

MVCshear

MVCshearMVCshear

ShearMVC

Intergranular

MVC

MVCshearMVCshear

MVCshear

MVCdelamMVCshear

MVCshear

MVCshear

MVCshear

Nishihara et al114

French and Weinrich89

Pugh and Green 123

Vajima et al149

Pugh and Green 123

Plumbridge et af121

HU93

ZOk152

ZOk152

Lewandowski etal189190

Liu andLewa ndowski103 195

Korbel et al99

Auger and Francois5051

Franklin et al84

Bridgman36

Ball et al53

Bullen et al64

Mellor and Wronski108

French andWeinrich88141

Vajima et al149

Pugh and Green 123

French and Weinrich85

Weinrich andFrench85141

Omura119

Bridgman36

ZOk152

Vajima et al149

Vajima et al149

Bridgman36

Dobromyslov et af79

Galli and Gibbs90

Kuvaldin et af100

Mellor and Wronski108

Spitzig 135

Vajima and Ishii147148

Vajima et al149

Ohmori et al118

Bullen et al65

Davidson andAnsell7576

Vajima et af149

Itoh et al95

Ohmori et al118

Worthington 144

Pugh and Green 123

Wagner et al140

Johnson et al97

Davidson et af74

McCann et al106

Brownrigg et al63

Johnson et af97

Spitzig et al133

Spitzig et al133

Plumbridge et al121

ZOk152

Spitzig et al134

Spitzig et al134

Johnson et al97

Zok and Embury152153

ZOk152

MoMoMoMoMo

7075AI-T47075AI-T6517075AI

Cu alloysPure

PureERCH CuLeaded brassa-brass a-fJ brass

70-30 40-60 brassy-brassCu-002BiCu-(15-40)ZnCu-(45-97)Ge

Ni alloyPure

bcc metalsCrCrCr

Mo

Fe-(O02-049)CMild steel (OOSC)Mild steel (O14C)Fe-3SiCast ironsSpheroidised cast iron101S steel1045 steel1045 steel1045 steel (spheroidised)4130 steel4310 steel4330 steel4360 steel4340 steelMaraging steelHV SO steelHV 130170180 steels01 tool steelTi-V steel

AI alloysPurePurePureAI-1 Si-07Mg-04MnAI-Cu-Mg-Si61S AI-T42014AI-T6AE2124AI-UAOAMB85-UAOA

6061AI-UAOA

Metals

Ferrous alloysSingle crystal FePure FePure FePure FeArmco FeFe-(0004-11)C

Mo Robbins andWronski131132

Cleavage 01-500

CRSS critical resolved shear stress delam delamination dadn crack propagation rate EI elongation HV Vickers hardness J J-integral MVC microvoidcoalescence UTS ultimate tensile strength

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 151

Table 2 (cant)

Pressure range

Materials Researcher(s) Failure mode P MPa Pj(fy Measured properties Note

Metalsbee metalsNb Bridgman36 01-2850 (ff qTa Bridgman36 01-2850 (ff [f

Ta Nishihara et al114 01-500 ayUTS rof Temperature upto 600C

Ta Robbins and Wronski131 1500 (fy Prepressu rised0-500

W Bridgman36 01-2840 af lofW Das and Radcliffe73 01-1100 0-15 (ff af lofW Daga71 01-1100 0-20 ay (ff qW Davidson et al74 CleavageMVCjshear 01-1600 qW Mellor and Wronski108 2800 (fy af EI Prepressu rised

prestrainedhcp metalsBe (PM) Aladag45 Intergranularj 01-980 af [f

Aldag et al46 transgranularBe (PM) Andrews and 01-2700 Prepressurised

Radcliffe49Be (ingot) Aladag45 Transgranular 01-980 0-38 (fy af [f

Aldag et al46

Be (castrolled) Bedere et al55 Intergranularj 01-1500 0-122 (ly af [f

transgranular shearCd Nakajima et al111 01-600 ayCo Davidson et al74 CleavagejMVCjshear 01-2350 f~Mg Davidson et aJ74 MVCjshear 01-1800 4Mg Pugh and Green 123 01-460 [fAZ91 (PM) Lahaie et al101 Intergranularshear 01-690 0-22 (fy ltofAZ91-T4jT6 Lewandowski et al193 01-380 af (f

Zn Davidson et al74 Brittlejplastic rupture qZn Pugh and Green 123 Cleavageplastic 01-138 ay q

ruptureZn-41AI Pugh and Green 123 01-410 ltofTi-7 AI-2Nb-1Ta (x) Johnson et al97 172 02 ay af lt1 Prepressu risedTi-6AI-4V (ajm Johnson et al97 172 02 (fy (ff Gf Prepressu risedTi-13V-l1 Cr-3AI (x) Johnson et al97 172 0middot2 ay af q Prepressurised

Metal matrix composites

AI matrix2014-20SiCp-T6jAE ZOk152 MVCshear 01-980 0-24 ay UTS Gf

2124-14SiCw-UAjOA ZOk152 MVCshear 01-690 0-20 ay UTS l12014-20SiCp-T6jAE Mahon et al198 MVCjshear 01-980 0-24 ay UTS l12124-14SiCw-UAjOA Vasudevan et al201 MVCjshear 01-690 0-20 ay UTS [f

MB85-15SiCp-UAjOA Lewandowski MVC 01-300 0-08 (ly af (fet al189190

M B85-15SiCp-UAjOA Liu 195 MVC 01-300 0-08 ay (ff q6061AI-15AI203-UAjOA Liu et al194195197 MVC 01-300 0-11 ay af q Damage

quantification6090AI-25AI203-SAjT6 Lewandowski et al193 MVC 01-400 GfMB78-15SiCp-UAjOA Singh and MVC 01-500 q Damage

Lewandowski199 quantificationA356-1 Oj20SiCp- T6 Embury et al184 MVC 01-850 q Damage

quantificationAI-AI3Ni Zok 152 MVC 01-690 0-45 ay UTS lt1

Mg matrixAZ91-20SiCp-T4 Lewandowski et al193 01-350 0-12 GfAZ91-19SiCp15 llm-T6 Lewandowski et al193 MVC 01-440 0-14 ay UTS af [f Damage

quantificationAZ91-20SiCp52 llm-T6 Lewandowski et al193 MVC 01-490 0-19 ay UTS af [f Damage

quantificationCu matrixCu-28W Zok152 MVC 01-690 UTSq

IntermetallicsNiAI Margevicius and Transgranularj 01-1400 0-140 (ly (ff Gf wj

Lewandowski155161163 inte rg ra nul ar PrepressurisedNiAI Weaver et al166167 Prepressu risedNi3AI Zok et al152170 Intergranular 01-965 af GfAI3Ti Witczak and Varin 169 2000 ay af lof HV PrepressurisedAmorphous metalsPd Cu Si Davis and Kavesh323 Shear 01-690 0-047 af EfZr Ti Ni Cu Be Lewandowski et al324 Shear 01-650 0-035 af Ff

CeramicsAI203 Bridgman36 2350-2960 afB203 Bridgman3637 2350-2960 af Gf density changeLiF Hanafee and 01-1300 Dislocation velocity

Radcliffe 176MgO Weaver and Brittlejshear 01-1000 ay af Ff

Paterson 180181NaCI Bridgman36 2350-2960 af [f

CRSS critical resolved shear stress delam delamination dajdn crack propagation rate EI elongation HV Vickers hardness J J-integral MVC microvoidcoalescence UTS ultimate tensile strength

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152 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

and any pressure variation reported during the testin addition to the load and strain measurementtechniques reported by the various investigators onthe materials listed Table 2 provides a similar list ofinvestigations organised by the type of material (egmetal intermetallic composite) tested as well as bythe crystal structure (eg bcc fcc hcp) of the metalsunder investigation Included in Table 2 are thespecific properties measured by each of the investi-gators and any comments related to the failure modespresent References to the works in Tables 1 and 2are provided while the specific data summariesappear in subsequent figures In most of the studieswhere testing is conducted with superimposed hydro-static pressure the specimens have been coated orjacketed274 with some impervious membrane (egpolymer Cu shrink fit tubing etc) in order to preventingress of the pressure medium into any surfacecracks porosity etc274 The membrane utilised istypically very thin and does not contribute signifi-cantly to the load bearing area of the specimenFurthermore pressurisation of specimens shieldedwith such membranes in and of itself has not pro-duced changes to the subsequent flow stress obtainedat atmospheric pressure

1

-2-1

o~ 1cr

2

3 Yield surface plotted in principal stress spacefor fully dense isotropic and homogeneousmaterial335336

(2)

(4)

(5)

ka = 511 + 512 + S13

kc = 2S13 + 533

shear stresses developed owing to the differences incompressibility between the matrix and the secondphase128 The maximum shear stress [max at thematrixsecond phase interface has been separatelyestimated by Das and Radcliffe73 and Ashby et al337

for a spherical particle and is given by

3Gm ( Km -Kp )[max = K 3K + 4G pm p m

where Gm is the shear modulus of the matrix Km

and K the bulk moduli of the matrix and the sec-ond phase respectively and P the applied hydro-static pressure Dislocations are generated when[max reaches the nucleation stress for dislocationgeneration which can be theoretically predicted ordetermined experimen tally338

Another manner in which shear stresses are gener-ated in polycrystalline materials through the simpleapplication of hydrostatic pressure is through theanisotropy of elastic constants91128 Crystals of allsystems except the cubic system can change shapewhen subjected to hydrostatic pressure cubic crystalshave isotropic bulk moduli The volume compress-ibility which is the inverse of the bulk modulus isthe pressure induced change in volume of a crystalnormalised to its original volume and the linearcompressibility k is the amount of pressure inducedlength change in a straight line normalised to itsoriginal length For the cubic system k is independentof orientation and is related to the elastic compliance5ij through

k = 511 + S12 bull bull bullbull bull (3)For the trigonal hexagonal and tetragonal systemstwo constants are required the value in the a directionka and the value in the c direction kc These compress-ibilities are related to the elastic compliance 5ij by

Effects of superimposed pressure onstress state in cylindrical specimensConditions present before necking incylindrical specimensPlastic deformation in metallic systems tested at lowhomologous temperatures primarily occurs via dislo-cation generation andor movement via shear stressesoften referred to as conservative motion or glidePlastic deformation under such conditions occurswhen the effective stress (j equals the yield strengthin tension (Jy where the effective stress is given as

- 1 ( )2 ( )2 ( )2] 120=0[(J1-(J2 + 02-(J3 + (J3-(J1

(1)and (Jb (J2 and (J3 represent the principal stressesThe application of a purely hydrostatic stress (ie(J1 = 02 = (J3) produces no shear stress in a homo-geneous and isotropic material as shown by the 3-Dyield surface plotted in stress space in Fig 3 Ahydrostatic stress is represented as the axis of thecylinder in Fig 3 and since such stresses never touchthe yield surface there should be no effect ofpressurisationpressure soaking on the subsequentflow behaviour when uniaxial testing is conducted atatmospheric pressure Pressurisation in this casedenotes the simple application of hydrostatic pressureto a material and its subsequent removal Thereshould similarly be little effect of superimposed press-ure on yielding when testing is conducted on acylindrical specimen in the presence of a confining(ie hydrostatic) pressure as the stress state up to theultimate tensile stress (UTS) (ie before necking) insuch specimens consists of the uniaxial stress plusany superimposed hydrostatic pressure

However simple pressurisation can serve as ameans for generating dislocations in a materialaround inclusions and other defects as there are local

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 153

1

4 Yield surface plotted in principal stress spacefor material containing void fraction of a 0057and b 0180 (Ref 336)

1

1

a~l 05cr

o~ta

-05

-1

-1

(a)

(b)

The linear compressibility in any other direction kris given by

kr = ka + (ke - ka)r2 (6)

where r is the direction cosine with subject to thec axis

If non-cubic metals can change shape because ofpressurisation then a random aggregate of manycrystals when subjected to unit hydrostatic pressurewill develop shear stresses across grain boundaries Itis this shear stress which produces dislocation gener-ation in anisotropic materials

The degree of anisotropy in these non-cubic systemsis given in terms of the ratio keka The anisotropy ofa number of hexagonal metals is given in Table 3Those metals with a high degree of anisotropy Cdand Zn have been shown91339 to require only modestlevels of pressure ( 300 MPa) to induce plastic strainin the grains while metals with ratios close to one(where a cubic metal equals 10) Zr and Mg requiredthe highest pressures ( 2middot6 GPa) to produce onlytrace amounts of plastic deformation Although TEManalyses have confirmed the presence of pressureinduced dislocations around inclusions in less pureFe and Fe-C alloys containing inclusions65139 highpurity cubic metals such as Cu AI Fe and Ni haveshown no such plastic deformation after pressuris-ation to levels up to 1 GPa (Refs 109 339)

Porous materials consisting of either interconnectedor isolated pores are also highly pressure sensitive340provided the pressure medium is shielded from thespecimen to prevent ingress of the pressure medium(ie gas liquid) into the pores The 3-D yield loci forsuch materials are distinctly different from that shownin Fig 3 for homogeneous and isotropic materialsShown in Fig 4 are 3-D yield loci for porous materialscontaining increasing levels of porosity335336341342It is clear that the application of a hydrostatic pressureof sufficient magnitude in these cases can touch theyield surface and thereby produce plastic flowExamples of such effects are provided in works onporous Fe (Refs 62 137)

where Oflow is the flow stress a the minimum specimenradius R the radius of curvature at the neck or notchand rn the distance from the centre along the planeof the neck

Since the notchneck geometry will often changewith additional deformation the level of triaxialtensile stress resulting from deformation of such

International Materials Reviews 1998 Vol 43 NO4

mens) when subsequently tested in tension also experi-ence triaxial tensile stresses in the neckednotchedregion In this case the major difference between thenecked region which evolved during deformation andthat simulated by prenotching a pristine (ie non-deformed) specimen relates to the differences indeformation history (and any damage) present in thenecked region as compared to the notched regionBridgman provided an estimate of the additionalhydrostatic tension OT in the plane of a neck ornotch2436 as

Conditions present past necking incylindrical specimensOnce a neck begins to form in a cylindrical tensilespecimen tested at atmospheric pressure triaxialtensile stresses develop in the necked region Boththe magnitude and location of such triaxial stressesvary with location in the neck which develops withadditional deformation Prenecked (eg notched speci-

Table 3 Linear compressibility and anisotropyfactors for some non-cubic materials(Refs 128 339)

Lattice ratioLinear compressibility MPa

Metal cia c axis ke a axis ka Ratio keka

Cadmium 18856 1890 x 106 217 X 106 870Zinc 18564 1341 x 106 201 X 106 670Bismuth 26095 1645 x 106 684 X 106 240Magnesium 16235 1016 x 106 1016 X 106 1middot00Zirconium 1middot5931 380 x 106 3middot80 X 106 1middot00Titanium 15870 270 x 106 270 X 106 100Beryllium 15684 227 x 106 291 X 106 078

(a 12 )

OT = Oflow In 1 + 2R - 2a~ (7)

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154 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Superimposed Hydrostatic Pressure MPa

4340 tenlpered 3000C 152

4340 tempered (eQ 5000C 152

4340 tempered 7000C 152

o 4310-Lower Yield 133

bullbull 4330-Lower Yield 113

6 01 Tool Steel Hard 152

6 01 Tool Steel Mediunl 152

6 01 Tool Steel Soft 152

[S ri-V Steel 9500C FRT 152

fpound Ti-V Steel 700degC FRT 15~

bull 7075AI-T651(TR) 5051

bull 7075AI-T65 I(WR) 5051

T 7075AI-T65I (RW) 5051

() 201411 1(21)

EE BY -80 1ower Yield 134

bull Maraging-Unaged (Ten) 134

bull Maraging-Unaged (Comp) ]34

bull Maraging-Aged (Ten) 134

bull1200

(a)

bullbull

1000

EB

[SJ

800600400200

bull bull bull bullbullbullII bullbull JI bullbull Q bullbull bull

~ 6III II II bull

j 6 i i6

o

20

o

=~~ 15Q)~~

rJ)

0

~ 10~

e~ 05Z

~~ 1500

2000

=~eJ)

~ 1000~~

rJ)

e-Q)

~

00(b)

(gt 2124J() () I

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure

5 Effect of pressure on yield strength of various bee and fcc metallic alloys

specimens will vary past necking in the cylindricalspecimen Thus while the level of superimposedhydrostatic pressure has been kept relatively constantin many of the studies listed in Tables 1 and 2 thetriaxial stresses present in the neck during tests withsuperimposed pressure will depend on a variety offactors including the neck geometry level of superim-posed pressure and the flow stress of the materialIt is important to note that some studies investigat-ing the effects of superimposed pressure on tensiontests have been conducted under conditions suchthat compressive triaxial stresses were present in thenecked region In these cases the levels of superim-posed pressure were high enough to overcome thetriaxial tensile stresses which developed in the evolv-ing neck Thus the ability to monitor visually thedevelopment of the neck during tests with superim-posed pressure as described above or conductinginterrupted tests where the neck can be physicallymeasured outside of the high pressure environmenthas some merits858689103197213

Effects of superimposed pressure onflow behaviourEffects of superimposed pressure onyield stressFigures 5-8 summarise published data on the effectsof pressurisationpressure soaking as well as tensiletesting at different levels of superimposed hydrostaticpressure on the yield strength typically reported asthe 0middot2 offset yield strength In the former tests theyield strength was measured at atmospheric pressureafter pressurisation while the measurements of yieldstress in the latter cases occurred during tensile testsconducted with superimposed hydrostatic pressureThe pressure medium utilised in the studies summar-ised was either an oil medium or Ar gas and wasconfirmed to be hydrostatic Figure 5 summarisesdata obtained on a variety of steels and aluminiumalloys while Fig 6 shows similar data obtained on avariety of single phase metals possessing a bcc crystalstructure Figure 7 is a plot of the same type of

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 155

___bull __ Ar111co Iron 65

5b 6b 7b and 8b are plots of the ratio of the yieldstrength obtained at pressure (or after pressure soak-ing) to that of the control material (ie no pressuresoaking) in the manner utilised by a number ofinvestigators henceforth this is called the normalisedyield strength Pressure independent yielding is rep-resented by the horizontal line at 1middot0 for the normal-ised yield strength in Figs 5b-8b It is clear fromFig 5a that a number of conventional structuralmetallic alloys exhibit nominally pressure independ-ent yielding behaviour as predicted by equation (1)Slight positive deviations for monolithic materials (ienormalised yield strengthgt 1 in Fig 5b) have beenexplained as in part due to the pressure depend-ence of the shear modulus which though modestis non-zero for various metallic materials136Models313314 have been developed to predict suchpressure dependent yielding in metallic materials andmetallic glasses321-323 and a few studies have invokedsuch models to explain such pressure dependence ofthe yield stress136 It should be noted that there havebeen observations of materials which exhibit muchgreater positive deviations than those of the monolithicmetals summarised in Fig 5a and b For example ithas been clearly shown that superimposed pressuresignificantly inhibits dislocation mobility in LiFthereby elevating the flow stress above that obtainedat atmospheric pressure176

It is also clear that some of the monolithic metalsshown in Fig 5a and b as well as a variety of bccmetals (cf Fig 6a and b) and certain chemistries ofthe intermetallic NiAI shown in Fig7a and b ex-hibit a significant decrease in the yield strength afterpressure soaking or during tests conducted withsuperimposed pressure In these cases the materialstypically exhibited a yield point and Liiders exten-sion before pressure soaking or testing with superim-posed pressure Pressurisation (andor testing withpressure) was shown to remove the yield pointand Liiders strain and thereby reduce the yieldstrength155157159161162166167as illustrated for castextruded NiAI in Fig 7c As shown in Figs 6a andband 7a and b large reductions in yield strengthwere obtained in Fe (Refs 65 147) Cr (Refs 59 6466 72) and commercially pure NiAI (Refs 155 157161-163) that had been cast and extruded ExtensiveTEM analyses in these cases revealed that pressureinduced dislocation generation occurred at non-metallic inclusions and other inhomogeneities in thesematerials6465155157158161an example of which isshown in Fig 7d (Ref 157) The generation of thesemobile pressure induced dislocations thereby reducedthe yield strength while subsequent thermal agingstudies conducted for sufficient time-temperaturecombinations at atmospheric pressure enabled relock-ing of the dislocations by interstitial impurities (egC) and a return of the yield point and Liidersstrain6465107147166as illustrated for NiAI in Fig7c(Ref 159) Similar studies166167 conducted on highpurity NiAI failed to reveal a yield point and anysubsequent effect of pressurisation on the yield stressas shown in Fig 7a and b consistent with sucharguments Pressurisation of the largest grained Fein Fig 6a and b (Ref 147) to increasingly higherpressures eventually produced excessive generation

International Materials Reviews 1998 Vol 43 NO4

1200

(a)

(b)

---)

1000800600

~_-----1-~ - --

400200

- - Chromium 64

bull - Iodide Chromium 72

Superimposed Hydrostatic Pressure MPa

bull ~ ~- Y- -y_~~~ - - -9

-------

cOil 15cQJ

000 10~~5 050Z

000

800

eo 700~~ 600pound 500eiJcCJ 400V)

0 300~~ 200

100o

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

20

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

6 Effeet of pressure on yield strength of variousbee metals GS grain size

--0 Fc GS=11Jlnl 147

-0 Fe GS=14Jlm 147

-[S- Fe GS=19Jlm 147

-83- - Fe GS=30Jlm 147

-- - Fe GS=450~lIn 147

6 - - PM T 72- ungsten

-pound --Arc-Melted Tunsten 72

information for the intermetallic NiAI which possessesa B2 (ie bcc derivative) crystal structure while Fig 8is a plot of data from more recent work on compositesbased on either aluminium or magnesium alloymatrixes The data reported for the control materials(ie no pressure soaking) occur on the ordinate at0middot1 MPa (ie atmospheric pressure) Figures 5a 6a7a and 8a summarise the reported values for theyield strength obtained either during tension testswith superimposed pressure or after pressure soakingat the levels of hydrostatic pressure indicated Figures

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156 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullNill Cast and extruded 161

-[S)- - CP-NiAI Prepressurised 166

-EB - - - HP NAlP d 166- 1 repressunse

- -- - - - NiAI-NPrepressurised 166

50

300

(a)

1500

EB

(b)

middotmiddotlSI

__

middotEB

-bullbull-

bull

1000

-----------

1

500

_------------ --- -_---

Superimposed Hydrostatic Pressure MPa

100

50

20

00

o

c~ 15QJl-rj~ 10~8~ 05Z

oo 500 1000 1500

Superimposed Hydrostatic Pressure MPa

el~~ 200

250

o annealedp ~a~~a p ~a~~a p ~~~aT = 200degC 2h T = 400degC 2h

Strain

(c)d

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure c stress-strain curvesof polycrystalline NiAI tested in tension after annealing at 82JOC for 2 h pressurised to 14 GPa and tested at atmospheric pressure and afteraging pressurised specimens at either 200degC or 400degC for 2 h (Ref 159) (arrows show proportional limit) d dislocations being punched from Zrinclusion in NiAI pressurised to 1middot4 GPa (Refs 156 157 160 161)

7 Effect of pressure on yield strength of NiAI

of dislocations and a slight increase in the yieldstrength because of work hardening Little effect ofpressurisation was 0bserved on higher strengthPowder metallurgy produced NiAI (cf Fig7a

International Materials Reviews 1998 Vol 43 No4

and b)166 or W as well as arc-melted W (cf Fig6aand b) 72 in part due to the higher strengths of thematerials tested and the limited range of pressuresutilised

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 157

500

600(a)

Effects of pressure on work hardeningexponent nThe effects of testing with superimposed pressureon the work hardening exponent n have beeninfrequently studied Figure 9a and b illustrates theexperimentally measured effect of superimposed press-ure on n for a high strength aluminium alloy(7075- T651) tested in different orientations withrespect to the rolling direction Testing was conductedwith superimposed pressure on either uniaxial tensionspecimens or plane strain tension specimens andgenerally revealed an increase in n with increasingpressure The authors5051 indicated that such obser-vations could be related to the amount of secondphase particles which could punch out dislocationloops because of their smaller compressibility in amanner analogous to that described above for thecomposite materials

yield stress apparently arises because of pressureinduced dislocation generation around the reinforce-ment which increases significantly the local dislo-cation density thereby providing local hardening anda higher yield strength192195196 Transmission elec-tron microscope studies have confirmed that suchevents can occur provided the pressurisation is con-ducted at a large enough pressure to generate shearstresses of sufficient magnitude near the reinforce-ment192 Testing with superimposed pressure has alsobeen shown to inhibit the accumulation of damage(eg void initiation and growth) in such materials Asthe accumulation of damage reduces the load bearingarea and instantaneous modulus in such compositesand thereby reduces the strain hardening rate press-ure induced damage suppression has been proposedas also contributing to the elevated flow stressesobtained during tests conducted with superimposedpressure192196201 This point is further discussedbelow when summarising the effects of confiningpressure on the UTS In addition recent work hasalso shown that the level of residual stress in thematrix and reinforcement can be changed via pressur-isation343344 Finally various models315-320 have indi-cated that the presence of the non-deformingreinforcement particles provides constrained flow andenhances the flow stress of the matrix The super-position of pressure during tension testing shouldcounteract this effect as illustrated in a fewpapers318-320

15001000

== 0---

~ - - - ---= = = t0- -- - -

(b)

500Superimposed Hydrostatic Pressure MPa

oo

20

EZ 05-

- --6--- 2014AI-20SiCp 13 Jlm-AE 152201

-J - - 2014AI-20SiCp 13 Jlm-T6 152201

-1- - - 2124AI-14SiCw 1 Jlrn-UA 152201

-T---- 2124AI-14SiCw 1 ~m-OA 152201

-X - AI-AI Ni l~m 1523

0-- IIOOAJ-IOAI)O_~ 193

ltgt 193- -- 1100AI-15Al)0 -

- -0- - - 6061AI-15AJ 0 13lrn-UA 1952 3

-- -0- -- 6061AI-15AI 0 (13lm-OA 1952 3

- - -[SJ- - - 6061AI-15At) 0 13~ln-UA 185_ 3

- - -EB- - - 6090AI-25SiCp-SA 193

- - -- - - 6090AI-25SiCp-T6 193

-0- AZ91-19SiCp 15~lTn-T6 193

-e- AZ91-20SiCp52-lIn-T6 J93

c ~~~1-~ 200l x~ -X- X- y

100

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

8 Effect of pressure on yield strength ofdiscontinuously reinforced metal matrixcomposites

The largest changes in the yield strength obtainedeither after pressurisation or during tests with super-imposed pressure have been exhibited by compositematerials as shown in Fig 8a and b (Refs 152 185191-196 198 200 201) One source of the enhanced

Superimposed Hydrostatic Pressure MPa

00o 500 1000 1500 Effects of pressure on UTS

The experimental data for the UTS obtained viatension testing with a range of superimposed pressuresare provided for both monolithic metals as well ascomposites in Figs 10-15 As indicated above thestress state at the UTS (ie before necking) in suchspecimens consists of the uniaxial stress plus anysuperimposed hydrostatic pressure Data obtainedfrom some of Bridgmans original works are providedin Figs 10-13 for a variety of ferrous based systemsheat treated to different strength levels and micro-structures Figure 14a summarises similar data for avariety of other ferrous and non-ferrous structuralmaterials Figure 14b provides the ratio of the UTS

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158 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-6- _ TR uniaxialmiddotmiddotAmiddot TR plane strain-0 --- TW uniaxial

----e TW plane strain-0 - WRuniaxialbull - WRplanc strain

- --0 RW uniaxial- -+- - RW plane strain

-fSJ- Fe-034C-O75Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-045C-O83Mn-OO l6P-O035S-O19Si (as-received)

o normalised l650degF---0 annealed fine-grained- -6- annealed coarse-grained

- - - - - brine-quenchedtenlpered 600degF- - -+- - - brine-quenchedtempered 600degF-- -bull- - -- brine-quenchedtempered 900degF

015 3000

3000

middot11bull

1500 2000 25001000500Superimposed Hydrostatic Pressure MPa

o-- -0--

-6---e----+- -

--SJ-- Fe-O68C-O 7lMn-OO l3P-O025S-O19Si (as-received)

----0 --- Fe-O9C-O47Mn-O015P-O036S-OllSi (as-received)normalised 1650degFannealed fine-grainedannealed coarse-grainedbrine-quenchedspherodisedbrine-quenchedtempered 600degFbrine-quenchedtenlpered 900degF

bullbullbull

oo

2500

500

ce~E 1500rrJ~J 1000

10 Effect of pressure on UTS of various steelstested by Bridgman36

600

(a)

500 600

500

IImiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

middot0-middot -0

400

400

0

300

300

200

200

(b)

100

100Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

bullbull - A R bullbull

~ bull ~

000o

= 200Q)

=oc0lt

~ 150~=2

Q)C

100tt==~ 050eoZ 000

o

a n v hydrostatic pressure b normalised n v superimposedhydrostatic pressure

9 Effect of pressure on strain hardening exponentn of 7075AI- T651 (Refs 50 51)

3000

11 Effect of pressure on UTS of various steelstested by Bridgman36

Superimposed Hydrostatic Pressure MPa

500o

o -0

1500 2000 2500 30001000500

bullbull middot11II bull

~o Q ~omiddot omiddot

6 middot0middot omiddotmiddotmiddot=ltgt 6

1000

2500

ri1~ 1500J

~ 2000E

obtained at high pressure to that obtained at atmos-pheric pressure and a normalised UTS of 1middot0 indicatesno measurable effect of superimposed pressure onthe UTS The data for the monolithic metalsshown in Figs 10-13 as well as those summar-ised in Fig 14a and b indicate that superimposedpressure generally has a relatively minor effect on theUTS of most monolithic metals though someexceptions are shown Figure 15a and b illustratesthat composite materials often exhibit significantpressure dependent values for the UTS This hasbeen attributed152185189-201 to the pressure inducedsuppression of damage associated with the reinforce-ment and the matrix (eg void initiationgrowthcoalescence) which is covered in more detail in thefollowing sections on fracture behaviour

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 159

Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

A-+

bull -- -

0middot ------ -----()---6 - - - -

-8

iJII

-4-

-8-

---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

-8--- -lt)-

--

1000

5000

4000

C~ 3000~rJ5

2000 l-3~0

o S - - ~ lJS

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

I I I I I Iii I i

- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

3000

2500 -

d )000 f~~ -

~ 1500

~ middot_cmiddot- ~1000 ~_ibullbullbullbullbull~ - - -- - -- --0

s ti

500

12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure llPa

Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

- - -fr-

---]--

----T-

---0--

- - -lS -

------ - --(gt

--+-0-

4340 tempered 3000e 152

4340 tempered 5000e I 52

4340 tempered 7000e 152

01 Tool Steel Hard 152

01 Tool Steel Medium 152

01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

o 2124AI-14SiCw IJlm-UA 152201

bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

-+ Cu-28W 152

- - - -() - - - AI- Al Ni 152-

800

- - - -----------

~z~~~---~-----~bull-----~200

(a)

ts------6---1---------------- ------~

(b)

20

oo 100 WO ~O 400 ~O WO mo WO

Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

05

100

1000

1000

(a)

(b)

800

800600

600400

400

lZ91 19i

200

200Superimposed Hydrostatic Pressure MPa

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot-[H

----- ------0--middot- ----0

------6--- --6- ----------fJ--- --6

-----[S]----- ----[S]

-1-- - - - - - gtJ- - - - - - -Y- - -- - - -I- - - - - - gtJ

- -_~ ~~-~----- ~ _

middotmiddot~~-plusmn~middot~1middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

Superimposed Hydrostatic Pressure MPa

(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

~~ 1500

rJ5~ 1000

500

00

20

1500~~8 10l-o0Z

05

000

categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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c Cs slJ) lJ)c Co 0uu

ooLO

oo~Ioo10

00o 10LO ~

oIN

o LO 0 LOO~OC)LOC)N

olt0en

0000000000C) bullbullbullbullbullbullbullbullbullbull fo bullbull

bullbullN bullbull

0000enen0 0lt0lt000bullbullN

00100000oOlooenlOLOO N coO) lt0 to

lJ)

20

Ql

c 0 c9 2 0lJ) bullbullbullbull enc Ql c~pound ~

0QllJ)

sectlJ)lJ) C C~ 9 0Q lJ) enQl C Ca ~ ~

CoenC

~

Co

coClcoQoa~u

lJ) e~ u

C C C (I)00pound Jen en Cl Cl

~~~~

coenc~

ClC0c(I)

Dc

c 00 enQC (I)

C)f-

CoenlJ)(I)aEoucoenC

~

C Co 0en enC C~~

c Co 0

u) enlJ) CIl(I) (I)a aE Eo 0u uc Co 0en enc c~~

~UJ

0CIlC

~CQl

E(I)

ucoQCIl0(I)0

~~gt~Ql

sectf-o3

Nll

ll

~ ~ ~ ll ~

~ sect ~ 1 ~ e~~~ ~Qic~O~co~B-g~-g~~~

~ ~ ~ ~ ~~ ~ g sect sect 5 ~~~~~~Ci~

q-

bullbullbull co~~Qi~e Ql ~

~ 0 ec E J~ pound Ezoo

~bullQl

CCcoUu2

too

Q

UQUiUlUiaLONIlttCO bullbullIenCON2ltt

ciuUiI

LOcoco2

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150 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Table 2 Summary of investigations on effects of hydrostatic pressure on mechanical behaviour ofinorganic materials - categorised by class of material

Pressu re range

Materials Researcher(s) Failure mode P MPa Measured properties Note

0-27 (UTS) Ef

Ef

Ef

0-15 (UTS) Ef void fraction0-19 (UTS) Ef void fraction

PrepressurisedprestrainedTemperature upto 600aC

Prepressurised

Prepressurisedprestrained

Interrupted testInterrupted test

Prepressurised

Prepressu rised

Prepressu rised

PrestrainedPrepressurised

Interrupted test

Prepressu rised

ay af poundf

ay

ay af EI

ay UTS 8f

Ef

(Iy af poundf

ay af EI

Ef

ay Ef EI n K1c

EI

Ef

Ef

qEf

dadn versus ~Kaf Ef

ay UTS Ef

(Iy UTS qay Ef

(Iy Ef voids quantification

ay af Ef

Ef

ay UTS nEf voids quantification(Iy af qay

ay

dadn versus ~Kay UTS Ef

ay

ay

ay (If Ef

ay UTS Ef

ay UTS Ef

Ef

ay EIEf

ay Ef

Ef

J

CRSS

0-58

0-12

0-270-12

0-7S

0-26

030-110-08

0-330-170-200-08

0-120-110-1S01-020-070-36

OS

0-103

01-500

01-3060

01-290001-S0001-140001-50002000

01-250001-31001000

01-600

01-6900-48001-60001-600

01-20001-296001-35001-80001-900

01-300

01-60001-52001-30001-62001-3501-92001-69001-69001-300

01-110001-60001-7

01-110001-S0001-69001-345100001-2250

01-70001-90001-345150001-69050017201-210001-126001-110017201-110001-110001-3501-69001-110001-110017201-69001-970

Cleavage

Cleavage

MVCshear

MVCshear

MVCshearMVCshear

ShearMVC

Intergranular

MVC

MVCshearMVCshear

MVCshear

MVCdelamMVCshear

MVCshear

MVCshear

MVCshear

Nishihara et al114

French and Weinrich89

Pugh and Green 123

Vajima et al149

Pugh and Green 123

Plumbridge et af121

HU93

ZOk152

ZOk152

Lewandowski etal189190

Liu andLewa ndowski103 195

Korbel et al99

Auger and Francois5051

Franklin et al84

Bridgman36

Ball et al53

Bullen et al64

Mellor and Wronski108

French andWeinrich88141

Vajima et al149

Pugh and Green 123

French and Weinrich85

Weinrich andFrench85141

Omura119

Bridgman36

ZOk152

Vajima et al149

Vajima et al149

Bridgman36

Dobromyslov et af79

Galli and Gibbs90

Kuvaldin et af100

Mellor and Wronski108

Spitzig 135

Vajima and Ishii147148

Vajima et al149

Ohmori et al118

Bullen et al65

Davidson andAnsell7576

Vajima et af149

Itoh et al95

Ohmori et al118

Worthington 144

Pugh and Green 123

Wagner et al140

Johnson et al97

Davidson et af74

McCann et al106

Brownrigg et al63

Johnson et af97

Spitzig et al133

Spitzig et al133

Plumbridge et al121

ZOk152

Spitzig et al134

Spitzig et al134

Johnson et al97

Zok and Embury152153

ZOk152

MoMoMoMoMo

7075AI-T47075AI-T6517075AI

Cu alloysPure

PureERCH CuLeaded brassa-brass a-fJ brass

70-30 40-60 brassy-brassCu-002BiCu-(15-40)ZnCu-(45-97)Ge

Ni alloyPure

bcc metalsCrCrCr

Mo

Fe-(O02-049)CMild steel (OOSC)Mild steel (O14C)Fe-3SiCast ironsSpheroidised cast iron101S steel1045 steel1045 steel1045 steel (spheroidised)4130 steel4310 steel4330 steel4360 steel4340 steelMaraging steelHV SO steelHV 130170180 steels01 tool steelTi-V steel

AI alloysPurePurePureAI-1 Si-07Mg-04MnAI-Cu-Mg-Si61S AI-T42014AI-T6AE2124AI-UAOAMB85-UAOA

6061AI-UAOA

Metals

Ferrous alloysSingle crystal FePure FePure FePure FeArmco FeFe-(0004-11)C

Mo Robbins andWronski131132

Cleavage 01-500

CRSS critical resolved shear stress delam delamination dadn crack propagation rate EI elongation HV Vickers hardness J J-integral MVC microvoidcoalescence UTS ultimate tensile strength

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 151

Table 2 (cant)

Pressure range

Materials Researcher(s) Failure mode P MPa Pj(fy Measured properties Note

Metalsbee metalsNb Bridgman36 01-2850 (ff qTa Bridgman36 01-2850 (ff [f

Ta Nishihara et al114 01-500 ayUTS rof Temperature upto 600C

Ta Robbins and Wronski131 1500 (fy Prepressu rised0-500

W Bridgman36 01-2840 af lofW Das and Radcliffe73 01-1100 0-15 (ff af lofW Daga71 01-1100 0-20 ay (ff qW Davidson et al74 CleavageMVCjshear 01-1600 qW Mellor and Wronski108 2800 (fy af EI Prepressu rised

prestrainedhcp metalsBe (PM) Aladag45 Intergranularj 01-980 af [f

Aldag et al46 transgranularBe (PM) Andrews and 01-2700 Prepressurised

Radcliffe49Be (ingot) Aladag45 Transgranular 01-980 0-38 (fy af [f

Aldag et al46

Be (castrolled) Bedere et al55 Intergranularj 01-1500 0-122 (ly af [f

transgranular shearCd Nakajima et al111 01-600 ayCo Davidson et al74 CleavagejMVCjshear 01-2350 f~Mg Davidson et aJ74 MVCjshear 01-1800 4Mg Pugh and Green 123 01-460 [fAZ91 (PM) Lahaie et al101 Intergranularshear 01-690 0-22 (fy ltofAZ91-T4jT6 Lewandowski et al193 01-380 af (f

Zn Davidson et al74 Brittlejplastic rupture qZn Pugh and Green 123 Cleavageplastic 01-138 ay q

ruptureZn-41AI Pugh and Green 123 01-410 ltofTi-7 AI-2Nb-1Ta (x) Johnson et al97 172 02 ay af lt1 Prepressu risedTi-6AI-4V (ajm Johnson et al97 172 02 (fy (ff Gf Prepressu risedTi-13V-l1 Cr-3AI (x) Johnson et al97 172 0middot2 ay af q Prepressurised

Metal matrix composites

AI matrix2014-20SiCp-T6jAE ZOk152 MVCshear 01-980 0-24 ay UTS Gf

2124-14SiCw-UAjOA ZOk152 MVCshear 01-690 0-20 ay UTS l12014-20SiCp-T6jAE Mahon et al198 MVCjshear 01-980 0-24 ay UTS l12124-14SiCw-UAjOA Vasudevan et al201 MVCjshear 01-690 0-20 ay UTS [f

MB85-15SiCp-UAjOA Lewandowski MVC 01-300 0-08 (ly af (fet al189190

M B85-15SiCp-UAjOA Liu 195 MVC 01-300 0-08 ay (ff q6061AI-15AI203-UAjOA Liu et al194195197 MVC 01-300 0-11 ay af q Damage

quantification6090AI-25AI203-SAjT6 Lewandowski et al193 MVC 01-400 GfMB78-15SiCp-UAjOA Singh and MVC 01-500 q Damage

Lewandowski199 quantificationA356-1 Oj20SiCp- T6 Embury et al184 MVC 01-850 q Damage

quantificationAI-AI3Ni Zok 152 MVC 01-690 0-45 ay UTS lt1

Mg matrixAZ91-20SiCp-T4 Lewandowski et al193 01-350 0-12 GfAZ91-19SiCp15 llm-T6 Lewandowski et al193 MVC 01-440 0-14 ay UTS af [f Damage

quantificationAZ91-20SiCp52 llm-T6 Lewandowski et al193 MVC 01-490 0-19 ay UTS af [f Damage

quantificationCu matrixCu-28W Zok152 MVC 01-690 UTSq

IntermetallicsNiAI Margevicius and Transgranularj 01-1400 0-140 (ly (ff Gf wj

Lewandowski155161163 inte rg ra nul ar PrepressurisedNiAI Weaver et al166167 Prepressu risedNi3AI Zok et al152170 Intergranular 01-965 af GfAI3Ti Witczak and Varin 169 2000 ay af lof HV PrepressurisedAmorphous metalsPd Cu Si Davis and Kavesh323 Shear 01-690 0-047 af EfZr Ti Ni Cu Be Lewandowski et al324 Shear 01-650 0-035 af Ff

CeramicsAI203 Bridgman36 2350-2960 afB203 Bridgman3637 2350-2960 af Gf density changeLiF Hanafee and 01-1300 Dislocation velocity

Radcliffe 176MgO Weaver and Brittlejshear 01-1000 ay af Ff

Paterson 180181NaCI Bridgman36 2350-2960 af [f

CRSS critical resolved shear stress delam delamination dajdn crack propagation rate EI elongation HV Vickers hardness J J-integral MVC microvoidcoalescence UTS ultimate tensile strength

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152 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

and any pressure variation reported during the testin addition to the load and strain measurementtechniques reported by the various investigators onthe materials listed Table 2 provides a similar list ofinvestigations organised by the type of material (egmetal intermetallic composite) tested as well as bythe crystal structure (eg bcc fcc hcp) of the metalsunder investigation Included in Table 2 are thespecific properties measured by each of the investi-gators and any comments related to the failure modespresent References to the works in Tables 1 and 2are provided while the specific data summariesappear in subsequent figures In most of the studieswhere testing is conducted with superimposed hydro-static pressure the specimens have been coated orjacketed274 with some impervious membrane (egpolymer Cu shrink fit tubing etc) in order to preventingress of the pressure medium into any surfacecracks porosity etc274 The membrane utilised istypically very thin and does not contribute signifi-cantly to the load bearing area of the specimenFurthermore pressurisation of specimens shieldedwith such membranes in and of itself has not pro-duced changes to the subsequent flow stress obtainedat atmospheric pressure

1

-2-1

o~ 1cr

2

3 Yield surface plotted in principal stress spacefor fully dense isotropic and homogeneousmaterial335336

(2)

(4)

(5)

ka = 511 + 512 + S13

kc = 2S13 + 533

shear stresses developed owing to the differences incompressibility between the matrix and the secondphase128 The maximum shear stress [max at thematrixsecond phase interface has been separatelyestimated by Das and Radcliffe73 and Ashby et al337

for a spherical particle and is given by

3Gm ( Km -Kp )[max = K 3K + 4G pm p m

where Gm is the shear modulus of the matrix Km

and K the bulk moduli of the matrix and the sec-ond phase respectively and P the applied hydro-static pressure Dislocations are generated when[max reaches the nucleation stress for dislocationgeneration which can be theoretically predicted ordetermined experimen tally338

Another manner in which shear stresses are gener-ated in polycrystalline materials through the simpleapplication of hydrostatic pressure is through theanisotropy of elastic constants91128 Crystals of allsystems except the cubic system can change shapewhen subjected to hydrostatic pressure cubic crystalshave isotropic bulk moduli The volume compress-ibility which is the inverse of the bulk modulus isthe pressure induced change in volume of a crystalnormalised to its original volume and the linearcompressibility k is the amount of pressure inducedlength change in a straight line normalised to itsoriginal length For the cubic system k is independentof orientation and is related to the elastic compliance5ij through

k = 511 + S12 bull bull bullbull bull (3)For the trigonal hexagonal and tetragonal systemstwo constants are required the value in the a directionka and the value in the c direction kc These compress-ibilities are related to the elastic compliance 5ij by

Effects of superimposed pressure onstress state in cylindrical specimensConditions present before necking incylindrical specimensPlastic deformation in metallic systems tested at lowhomologous temperatures primarily occurs via dislo-cation generation andor movement via shear stressesoften referred to as conservative motion or glidePlastic deformation under such conditions occurswhen the effective stress (j equals the yield strengthin tension (Jy where the effective stress is given as

- 1 ( )2 ( )2 ( )2] 120=0[(J1-(J2 + 02-(J3 + (J3-(J1

(1)and (Jb (J2 and (J3 represent the principal stressesThe application of a purely hydrostatic stress (ie(J1 = 02 = (J3) produces no shear stress in a homo-geneous and isotropic material as shown by the 3-Dyield surface plotted in stress space in Fig 3 Ahydrostatic stress is represented as the axis of thecylinder in Fig 3 and since such stresses never touchthe yield surface there should be no effect ofpressurisationpressure soaking on the subsequentflow behaviour when uniaxial testing is conducted atatmospheric pressure Pressurisation in this casedenotes the simple application of hydrostatic pressureto a material and its subsequent removal Thereshould similarly be little effect of superimposed press-ure on yielding when testing is conducted on acylindrical specimen in the presence of a confining(ie hydrostatic) pressure as the stress state up to theultimate tensile stress (UTS) (ie before necking) insuch specimens consists of the uniaxial stress plusany superimposed hydrostatic pressure

However simple pressurisation can serve as ameans for generating dislocations in a materialaround inclusions and other defects as there are local

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 153

1

4 Yield surface plotted in principal stress spacefor material containing void fraction of a 0057and b 0180 (Ref 336)

1

1

a~l 05cr

o~ta

-05

-1

-1

(a)

(b)

The linear compressibility in any other direction kris given by

kr = ka + (ke - ka)r2 (6)

where r is the direction cosine with subject to thec axis

If non-cubic metals can change shape because ofpressurisation then a random aggregate of manycrystals when subjected to unit hydrostatic pressurewill develop shear stresses across grain boundaries Itis this shear stress which produces dislocation gener-ation in anisotropic materials

The degree of anisotropy in these non-cubic systemsis given in terms of the ratio keka The anisotropy ofa number of hexagonal metals is given in Table 3Those metals with a high degree of anisotropy Cdand Zn have been shown91339 to require only modestlevels of pressure ( 300 MPa) to induce plastic strainin the grains while metals with ratios close to one(where a cubic metal equals 10) Zr and Mg requiredthe highest pressures ( 2middot6 GPa) to produce onlytrace amounts of plastic deformation Although TEManalyses have confirmed the presence of pressureinduced dislocations around inclusions in less pureFe and Fe-C alloys containing inclusions65139 highpurity cubic metals such as Cu AI Fe and Ni haveshown no such plastic deformation after pressuris-ation to levels up to 1 GPa (Refs 109 339)

Porous materials consisting of either interconnectedor isolated pores are also highly pressure sensitive340provided the pressure medium is shielded from thespecimen to prevent ingress of the pressure medium(ie gas liquid) into the pores The 3-D yield loci forsuch materials are distinctly different from that shownin Fig 3 for homogeneous and isotropic materialsShown in Fig 4 are 3-D yield loci for porous materialscontaining increasing levels of porosity335336341342It is clear that the application of a hydrostatic pressureof sufficient magnitude in these cases can touch theyield surface and thereby produce plastic flowExamples of such effects are provided in works onporous Fe (Refs 62 137)

where Oflow is the flow stress a the minimum specimenradius R the radius of curvature at the neck or notchand rn the distance from the centre along the planeof the neck

Since the notchneck geometry will often changewith additional deformation the level of triaxialtensile stress resulting from deformation of such

International Materials Reviews 1998 Vol 43 NO4

mens) when subsequently tested in tension also experi-ence triaxial tensile stresses in the neckednotchedregion In this case the major difference between thenecked region which evolved during deformation andthat simulated by prenotching a pristine (ie non-deformed) specimen relates to the differences indeformation history (and any damage) present in thenecked region as compared to the notched regionBridgman provided an estimate of the additionalhydrostatic tension OT in the plane of a neck ornotch2436 as

Conditions present past necking incylindrical specimensOnce a neck begins to form in a cylindrical tensilespecimen tested at atmospheric pressure triaxialtensile stresses develop in the necked region Boththe magnitude and location of such triaxial stressesvary with location in the neck which develops withadditional deformation Prenecked (eg notched speci-

Table 3 Linear compressibility and anisotropyfactors for some non-cubic materials(Refs 128 339)

Lattice ratioLinear compressibility MPa

Metal cia c axis ke a axis ka Ratio keka

Cadmium 18856 1890 x 106 217 X 106 870Zinc 18564 1341 x 106 201 X 106 670Bismuth 26095 1645 x 106 684 X 106 240Magnesium 16235 1016 x 106 1016 X 106 1middot00Zirconium 1middot5931 380 x 106 3middot80 X 106 1middot00Titanium 15870 270 x 106 270 X 106 100Beryllium 15684 227 x 106 291 X 106 078

(a 12 )

OT = Oflow In 1 + 2R - 2a~ (7)

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154 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Superimposed Hydrostatic Pressure MPa

4340 tenlpered 3000C 152

4340 tempered (eQ 5000C 152

4340 tempered 7000C 152

o 4310-Lower Yield 133

bullbull 4330-Lower Yield 113

6 01 Tool Steel Hard 152

6 01 Tool Steel Mediunl 152

6 01 Tool Steel Soft 152

[S ri-V Steel 9500C FRT 152

fpound Ti-V Steel 700degC FRT 15~

bull 7075AI-T651(TR) 5051

bull 7075AI-T65 I(WR) 5051

T 7075AI-T65I (RW) 5051

() 201411 1(21)

EE BY -80 1ower Yield 134

bull Maraging-Unaged (Ten) 134

bull Maraging-Unaged (Comp) ]34

bull Maraging-Aged (Ten) 134

bull1200

(a)

bullbull

1000

EB

[SJ

800600400200

bull bull bull bullbullbullII bullbull JI bullbull Q bullbull bull

~ 6III II II bull

j 6 i i6

o

20

o

=~~ 15Q)~~

rJ)

0

~ 10~

e~ 05Z

~~ 1500

2000

=~eJ)

~ 1000~~

rJ)

e-Q)

~

00(b)

(gt 2124J() () I

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure

5 Effect of pressure on yield strength of various bee and fcc metallic alloys

specimens will vary past necking in the cylindricalspecimen Thus while the level of superimposedhydrostatic pressure has been kept relatively constantin many of the studies listed in Tables 1 and 2 thetriaxial stresses present in the neck during tests withsuperimposed pressure will depend on a variety offactors including the neck geometry level of superim-posed pressure and the flow stress of the materialIt is important to note that some studies investigat-ing the effects of superimposed pressure on tensiontests have been conducted under conditions suchthat compressive triaxial stresses were present in thenecked region In these cases the levels of superim-posed pressure were high enough to overcome thetriaxial tensile stresses which developed in the evolv-ing neck Thus the ability to monitor visually thedevelopment of the neck during tests with superim-posed pressure as described above or conductinginterrupted tests where the neck can be physicallymeasured outside of the high pressure environmenthas some merits858689103197213

Effects of superimposed pressure onflow behaviourEffects of superimposed pressure onyield stressFigures 5-8 summarise published data on the effectsof pressurisationpressure soaking as well as tensiletesting at different levels of superimposed hydrostaticpressure on the yield strength typically reported asthe 0middot2 offset yield strength In the former tests theyield strength was measured at atmospheric pressureafter pressurisation while the measurements of yieldstress in the latter cases occurred during tensile testsconducted with superimposed hydrostatic pressureThe pressure medium utilised in the studies summar-ised was either an oil medium or Ar gas and wasconfirmed to be hydrostatic Figure 5 summarisesdata obtained on a variety of steels and aluminiumalloys while Fig 6 shows similar data obtained on avariety of single phase metals possessing a bcc crystalstructure Figure 7 is a plot of the same type of

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 155

___bull __ Ar111co Iron 65

5b 6b 7b and 8b are plots of the ratio of the yieldstrength obtained at pressure (or after pressure soak-ing) to that of the control material (ie no pressuresoaking) in the manner utilised by a number ofinvestigators henceforth this is called the normalisedyield strength Pressure independent yielding is rep-resented by the horizontal line at 1middot0 for the normal-ised yield strength in Figs 5b-8b It is clear fromFig 5a that a number of conventional structuralmetallic alloys exhibit nominally pressure independ-ent yielding behaviour as predicted by equation (1)Slight positive deviations for monolithic materials (ienormalised yield strengthgt 1 in Fig 5b) have beenexplained as in part due to the pressure depend-ence of the shear modulus which though modestis non-zero for various metallic materials136Models313314 have been developed to predict suchpressure dependent yielding in metallic materials andmetallic glasses321-323 and a few studies have invokedsuch models to explain such pressure dependence ofthe yield stress136 It should be noted that there havebeen observations of materials which exhibit muchgreater positive deviations than those of the monolithicmetals summarised in Fig 5a and b For example ithas been clearly shown that superimposed pressuresignificantly inhibits dislocation mobility in LiFthereby elevating the flow stress above that obtainedat atmospheric pressure176

It is also clear that some of the monolithic metalsshown in Fig 5a and b as well as a variety of bccmetals (cf Fig 6a and b) and certain chemistries ofthe intermetallic NiAI shown in Fig7a and b ex-hibit a significant decrease in the yield strength afterpressure soaking or during tests conducted withsuperimposed pressure In these cases the materialstypically exhibited a yield point and Liiders exten-sion before pressure soaking or testing with superim-posed pressure Pressurisation (andor testing withpressure) was shown to remove the yield pointand Liiders strain and thereby reduce the yieldstrength155157159161162166167as illustrated for castextruded NiAI in Fig 7c As shown in Figs 6a andband 7a and b large reductions in yield strengthwere obtained in Fe (Refs 65 147) Cr (Refs 59 6466 72) and commercially pure NiAI (Refs 155 157161-163) that had been cast and extruded ExtensiveTEM analyses in these cases revealed that pressureinduced dislocation generation occurred at non-metallic inclusions and other inhomogeneities in thesematerials6465155157158161an example of which isshown in Fig 7d (Ref 157) The generation of thesemobile pressure induced dislocations thereby reducedthe yield strength while subsequent thermal agingstudies conducted for sufficient time-temperaturecombinations at atmospheric pressure enabled relock-ing of the dislocations by interstitial impurities (egC) and a return of the yield point and Liidersstrain6465107147166as illustrated for NiAI in Fig7c(Ref 159) Similar studies166167 conducted on highpurity NiAI failed to reveal a yield point and anysubsequent effect of pressurisation on the yield stressas shown in Fig 7a and b consistent with sucharguments Pressurisation of the largest grained Fein Fig 6a and b (Ref 147) to increasingly higherpressures eventually produced excessive generation

International Materials Reviews 1998 Vol 43 NO4

1200

(a)

(b)

---)

1000800600

~_-----1-~ - --

400200

- - Chromium 64

bull - Iodide Chromium 72

Superimposed Hydrostatic Pressure MPa

bull ~ ~- Y- -y_~~~ - - -9

-------

cOil 15cQJ

000 10~~5 050Z

000

800

eo 700~~ 600pound 500eiJcCJ 400V)

0 300~~ 200

100o

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

20

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

6 Effeet of pressure on yield strength of variousbee metals GS grain size

--0 Fc GS=11Jlnl 147

-0 Fe GS=14Jlm 147

-[S- Fe GS=19Jlm 147

-83- - Fe GS=30Jlm 147

-- - Fe GS=450~lIn 147

6 - - PM T 72- ungsten

-pound --Arc-Melted Tunsten 72

information for the intermetallic NiAI which possessesa B2 (ie bcc derivative) crystal structure while Fig 8is a plot of data from more recent work on compositesbased on either aluminium or magnesium alloymatrixes The data reported for the control materials(ie no pressure soaking) occur on the ordinate at0middot1 MPa (ie atmospheric pressure) Figures 5a 6a7a and 8a summarise the reported values for theyield strength obtained either during tension testswith superimposed pressure or after pressure soakingat the levels of hydrostatic pressure indicated Figures

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156 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullNill Cast and extruded 161

-[S)- - CP-NiAI Prepressurised 166

-EB - - - HP NAlP d 166- 1 repressunse

- -- - - - NiAI-NPrepressurised 166

50

300

(a)

1500

EB

(b)

middotmiddotlSI

__

middotEB

-bullbull-

bull

1000

-----------

1

500

_------------ --- -_---

Superimposed Hydrostatic Pressure MPa

100

50

20

00

o

c~ 15QJl-rj~ 10~8~ 05Z

oo 500 1000 1500

Superimposed Hydrostatic Pressure MPa

el~~ 200

250

o annealedp ~a~~a p ~a~~a p ~~~aT = 200degC 2h T = 400degC 2h

Strain

(c)d

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure c stress-strain curvesof polycrystalline NiAI tested in tension after annealing at 82JOC for 2 h pressurised to 14 GPa and tested at atmospheric pressure and afteraging pressurised specimens at either 200degC or 400degC for 2 h (Ref 159) (arrows show proportional limit) d dislocations being punched from Zrinclusion in NiAI pressurised to 1middot4 GPa (Refs 156 157 160 161)

7 Effect of pressure on yield strength of NiAI

of dislocations and a slight increase in the yieldstrength because of work hardening Little effect ofpressurisation was 0bserved on higher strengthPowder metallurgy produced NiAI (cf Fig7a

International Materials Reviews 1998 Vol 43 No4

and b)166 or W as well as arc-melted W (cf Fig6aand b) 72 in part due to the higher strengths of thematerials tested and the limited range of pressuresutilised

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 157

500

600(a)

Effects of pressure on work hardeningexponent nThe effects of testing with superimposed pressureon the work hardening exponent n have beeninfrequently studied Figure 9a and b illustrates theexperimentally measured effect of superimposed press-ure on n for a high strength aluminium alloy(7075- T651) tested in different orientations withrespect to the rolling direction Testing was conductedwith superimposed pressure on either uniaxial tensionspecimens or plane strain tension specimens andgenerally revealed an increase in n with increasingpressure The authors5051 indicated that such obser-vations could be related to the amount of secondphase particles which could punch out dislocationloops because of their smaller compressibility in amanner analogous to that described above for thecomposite materials

yield stress apparently arises because of pressureinduced dislocation generation around the reinforce-ment which increases significantly the local dislo-cation density thereby providing local hardening anda higher yield strength192195196 Transmission elec-tron microscope studies have confirmed that suchevents can occur provided the pressurisation is con-ducted at a large enough pressure to generate shearstresses of sufficient magnitude near the reinforce-ment192 Testing with superimposed pressure has alsobeen shown to inhibit the accumulation of damage(eg void initiation and growth) in such materials Asthe accumulation of damage reduces the load bearingarea and instantaneous modulus in such compositesand thereby reduces the strain hardening rate press-ure induced damage suppression has been proposedas also contributing to the elevated flow stressesobtained during tests conducted with superimposedpressure192196201 This point is further discussedbelow when summarising the effects of confiningpressure on the UTS In addition recent work hasalso shown that the level of residual stress in thematrix and reinforcement can be changed via pressur-isation343344 Finally various models315-320 have indi-cated that the presence of the non-deformingreinforcement particles provides constrained flow andenhances the flow stress of the matrix The super-position of pressure during tension testing shouldcounteract this effect as illustrated in a fewpapers318-320

15001000

== 0---

~ - - - ---= = = t0- -- - -

(b)

500Superimposed Hydrostatic Pressure MPa

oo

20

EZ 05-

- --6--- 2014AI-20SiCp 13 Jlm-AE 152201

-J - - 2014AI-20SiCp 13 Jlm-T6 152201

-1- - - 2124AI-14SiCw 1 Jlrn-UA 152201

-T---- 2124AI-14SiCw 1 ~m-OA 152201

-X - AI-AI Ni l~m 1523

0-- IIOOAJ-IOAI)O_~ 193

ltgt 193- -- 1100AI-15Al)0 -

- -0- - - 6061AI-15AJ 0 13lrn-UA 1952 3

-- -0- -- 6061AI-15AI 0 (13lm-OA 1952 3

- - -[SJ- - - 6061AI-15At) 0 13~ln-UA 185_ 3

- - -EB- - - 6090AI-25SiCp-SA 193

- - -- - - 6090AI-25SiCp-T6 193

-0- AZ91-19SiCp 15~lTn-T6 193

-e- AZ91-20SiCp52-lIn-T6 J93

c ~~~1-~ 200l x~ -X- X- y

100

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

8 Effect of pressure on yield strength ofdiscontinuously reinforced metal matrixcomposites

The largest changes in the yield strength obtainedeither after pressurisation or during tests with super-imposed pressure have been exhibited by compositematerials as shown in Fig 8a and b (Refs 152 185191-196 198 200 201) One source of the enhanced

Superimposed Hydrostatic Pressure MPa

00o 500 1000 1500 Effects of pressure on UTS

The experimental data for the UTS obtained viatension testing with a range of superimposed pressuresare provided for both monolithic metals as well ascomposites in Figs 10-15 As indicated above thestress state at the UTS (ie before necking) in suchspecimens consists of the uniaxial stress plus anysuperimposed hydrostatic pressure Data obtainedfrom some of Bridgmans original works are providedin Figs 10-13 for a variety of ferrous based systemsheat treated to different strength levels and micro-structures Figure 14a summarises similar data for avariety of other ferrous and non-ferrous structuralmaterials Figure 14b provides the ratio of the UTS

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158 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-6- _ TR uniaxialmiddotmiddotAmiddot TR plane strain-0 --- TW uniaxial

----e TW plane strain-0 - WRuniaxialbull - WRplanc strain

- --0 RW uniaxial- -+- - RW plane strain

-fSJ- Fe-034C-O75Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-045C-O83Mn-OO l6P-O035S-O19Si (as-received)

o normalised l650degF---0 annealed fine-grained- -6- annealed coarse-grained

- - - - - brine-quenchedtenlpered 600degF- - -+- - - brine-quenchedtempered 600degF-- -bull- - -- brine-quenchedtempered 900degF

015 3000

3000

middot11bull

1500 2000 25001000500Superimposed Hydrostatic Pressure MPa

o-- -0--

-6---e----+- -

--SJ-- Fe-O68C-O 7lMn-OO l3P-O025S-O19Si (as-received)

----0 --- Fe-O9C-O47Mn-O015P-O036S-OllSi (as-received)normalised 1650degFannealed fine-grainedannealed coarse-grainedbrine-quenchedspherodisedbrine-quenchedtempered 600degFbrine-quenchedtenlpered 900degF

bullbullbull

oo

2500

500

ce~E 1500rrJ~J 1000

10 Effect of pressure on UTS of various steelstested by Bridgman36

600

(a)

500 600

500

IImiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

middot0-middot -0

400

400

0

300

300

200

200

(b)

100

100Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

bullbull - A R bullbull

~ bull ~

000o

= 200Q)

=oc0lt

~ 150~=2

Q)C

100tt==~ 050eoZ 000

o

a n v hydrostatic pressure b normalised n v superimposedhydrostatic pressure

9 Effect of pressure on strain hardening exponentn of 7075AI- T651 (Refs 50 51)

3000

11 Effect of pressure on UTS of various steelstested by Bridgman36

Superimposed Hydrostatic Pressure MPa

500o

o -0

1500 2000 2500 30001000500

bullbull middot11II bull

~o Q ~omiddot omiddot

6 middot0middot omiddotmiddotmiddot=ltgt 6

1000

2500

ri1~ 1500J

~ 2000E

obtained at high pressure to that obtained at atmos-pheric pressure and a normalised UTS of 1middot0 indicatesno measurable effect of superimposed pressure onthe UTS The data for the monolithic metalsshown in Figs 10-13 as well as those summar-ised in Fig 14a and b indicate that superimposedpressure generally has a relatively minor effect on theUTS of most monolithic metals though someexceptions are shown Figure 15a and b illustratesthat composite materials often exhibit significantpressure dependent values for the UTS This hasbeen attributed152185189-201 to the pressure inducedsuppression of damage associated with the reinforce-ment and the matrix (eg void initiationgrowthcoalescence) which is covered in more detail in thefollowing sections on fracture behaviour

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Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

A-+

bull -- -

0middot ------ -----()---6 - - - -

-8

iJII

-4-

-8-

---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

-8--- -lt)-

--

1000

5000

4000

C~ 3000~rJ5

2000 l-3~0

o S - - ~ lJS

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

I I I I I Iii I i

- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

3000

2500 -

d )000 f~~ -

~ 1500

~ middot_cmiddot- ~1000 ~_ibullbullbullbullbull~ - - -- - -- --0

s ti

500

12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure llPa

Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

- - -fr-

---]--

----T-

---0--

- - -lS -

------ - --(gt

--+-0-

4340 tempered 3000e 152

4340 tempered 5000e I 52

4340 tempered 7000e 152

01 Tool Steel Hard 152

01 Tool Steel Medium 152

01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

o 2124AI-14SiCw IJlm-UA 152201

bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

-+ Cu-28W 152

- - - -() - - - AI- Al Ni 152-

800

- - - -----------

~z~~~---~-----~bull-----~200

(a)

ts------6---1---------------- ------~

(b)

20

oo 100 WO ~O 400 ~O WO mo WO

Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

05

100

1000

1000

(a)

(b)

800

800600

600400

400

lZ91 19i

200

200Superimposed Hydrostatic Pressure MPa

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot-[H

----- ------0--middot- ----0

------6--- --6- ----------fJ--- --6

-----[S]----- ----[S]

-1-- - - - - - gtJ- - - - - - -Y- - -- - - -I- - - - - - gtJ

- -_~ ~~-~----- ~ _

middotmiddot~~-plusmn~middot~1middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

Superimposed Hydrostatic Pressure MPa

(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

~~ 1500

rJ5~ 1000

500

00

20

1500~~8 10l-o0Z

05

000

categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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150 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Table 2 Summary of investigations on effects of hydrostatic pressure on mechanical behaviour ofinorganic materials - categorised by class of material

Pressu re range

Materials Researcher(s) Failure mode P MPa Measured properties Note

0-27 (UTS) Ef

Ef

Ef

0-15 (UTS) Ef void fraction0-19 (UTS) Ef void fraction

PrepressurisedprestrainedTemperature upto 600aC

Prepressurised

Prepressurisedprestrained

Interrupted testInterrupted test

Prepressurised

Prepressu rised

Prepressu rised

PrestrainedPrepressurised

Interrupted test

Prepressu rised

ay af poundf

ay

ay af EI

ay UTS 8f

Ef

(Iy af poundf

ay af EI

Ef

ay Ef EI n K1c

EI

Ef

Ef

qEf

dadn versus ~Kaf Ef

ay UTS Ef

(Iy UTS qay Ef

(Iy Ef voids quantification

ay af Ef

Ef

ay UTS nEf voids quantification(Iy af qay

ay

dadn versus ~Kay UTS Ef

ay

ay

ay (If Ef

ay UTS Ef

ay UTS Ef

Ef

ay EIEf

ay Ef

Ef

J

CRSS

0-58

0-12

0-270-12

0-7S

0-26

030-110-08

0-330-170-200-08

0-120-110-1S01-020-070-36

OS

0-103

01-500

01-3060

01-290001-S0001-140001-50002000

01-250001-31001000

01-600

01-6900-48001-60001-600

01-20001-296001-35001-80001-900

01-300

01-60001-52001-30001-62001-3501-92001-69001-69001-300

01-110001-60001-7

01-110001-S0001-69001-345100001-2250

01-70001-90001-345150001-69050017201-210001-126001-110017201-110001-110001-3501-69001-110001-110017201-69001-970

Cleavage

Cleavage

MVCshear

MVCshear

MVCshearMVCshear

ShearMVC

Intergranular

MVC

MVCshearMVCshear

MVCshear

MVCdelamMVCshear

MVCshear

MVCshear

MVCshear

Nishihara et al114

French and Weinrich89

Pugh and Green 123

Vajima et al149

Pugh and Green 123

Plumbridge et af121

HU93

ZOk152

ZOk152

Lewandowski etal189190

Liu andLewa ndowski103 195

Korbel et al99

Auger and Francois5051

Franklin et al84

Bridgman36

Ball et al53

Bullen et al64

Mellor and Wronski108

French andWeinrich88141

Vajima et al149

Pugh and Green 123

French and Weinrich85

Weinrich andFrench85141

Omura119

Bridgman36

ZOk152

Vajima et al149

Vajima et al149

Bridgman36

Dobromyslov et af79

Galli and Gibbs90

Kuvaldin et af100

Mellor and Wronski108

Spitzig 135

Vajima and Ishii147148

Vajima et al149

Ohmori et al118

Bullen et al65

Davidson andAnsell7576

Vajima et af149

Itoh et al95

Ohmori et al118

Worthington 144

Pugh and Green 123

Wagner et al140

Johnson et al97

Davidson et af74

McCann et al106

Brownrigg et al63

Johnson et af97

Spitzig et al133

Spitzig et al133

Plumbridge et al121

ZOk152

Spitzig et al134

Spitzig et al134

Johnson et al97

Zok and Embury152153

ZOk152

MoMoMoMoMo

7075AI-T47075AI-T6517075AI

Cu alloysPure

PureERCH CuLeaded brassa-brass a-fJ brass

70-30 40-60 brassy-brassCu-002BiCu-(15-40)ZnCu-(45-97)Ge

Ni alloyPure

bcc metalsCrCrCr

Mo

Fe-(O02-049)CMild steel (OOSC)Mild steel (O14C)Fe-3SiCast ironsSpheroidised cast iron101S steel1045 steel1045 steel1045 steel (spheroidised)4130 steel4310 steel4330 steel4360 steel4340 steelMaraging steelHV SO steelHV 130170180 steels01 tool steelTi-V steel

AI alloysPurePurePureAI-1 Si-07Mg-04MnAI-Cu-Mg-Si61S AI-T42014AI-T6AE2124AI-UAOAMB85-UAOA

6061AI-UAOA

Metals

Ferrous alloysSingle crystal FePure FePure FePure FeArmco FeFe-(0004-11)C

Mo Robbins andWronski131132

Cleavage 01-500

CRSS critical resolved shear stress delam delamination dadn crack propagation rate EI elongation HV Vickers hardness J J-integral MVC microvoidcoalescence UTS ultimate tensile strength

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 151

Table 2 (cant)

Pressure range

Materials Researcher(s) Failure mode P MPa Pj(fy Measured properties Note

Metalsbee metalsNb Bridgman36 01-2850 (ff qTa Bridgman36 01-2850 (ff [f

Ta Nishihara et al114 01-500 ayUTS rof Temperature upto 600C

Ta Robbins and Wronski131 1500 (fy Prepressu rised0-500

W Bridgman36 01-2840 af lofW Das and Radcliffe73 01-1100 0-15 (ff af lofW Daga71 01-1100 0-20 ay (ff qW Davidson et al74 CleavageMVCjshear 01-1600 qW Mellor and Wronski108 2800 (fy af EI Prepressu rised

prestrainedhcp metalsBe (PM) Aladag45 Intergranularj 01-980 af [f

Aldag et al46 transgranularBe (PM) Andrews and 01-2700 Prepressurised

Radcliffe49Be (ingot) Aladag45 Transgranular 01-980 0-38 (fy af [f

Aldag et al46

Be (castrolled) Bedere et al55 Intergranularj 01-1500 0-122 (ly af [f

transgranular shearCd Nakajima et al111 01-600 ayCo Davidson et al74 CleavagejMVCjshear 01-2350 f~Mg Davidson et aJ74 MVCjshear 01-1800 4Mg Pugh and Green 123 01-460 [fAZ91 (PM) Lahaie et al101 Intergranularshear 01-690 0-22 (fy ltofAZ91-T4jT6 Lewandowski et al193 01-380 af (f

Zn Davidson et al74 Brittlejplastic rupture qZn Pugh and Green 123 Cleavageplastic 01-138 ay q

ruptureZn-41AI Pugh and Green 123 01-410 ltofTi-7 AI-2Nb-1Ta (x) Johnson et al97 172 02 ay af lt1 Prepressu risedTi-6AI-4V (ajm Johnson et al97 172 02 (fy (ff Gf Prepressu risedTi-13V-l1 Cr-3AI (x) Johnson et al97 172 0middot2 ay af q Prepressurised

Metal matrix composites

AI matrix2014-20SiCp-T6jAE ZOk152 MVCshear 01-980 0-24 ay UTS Gf

2124-14SiCw-UAjOA ZOk152 MVCshear 01-690 0-20 ay UTS l12014-20SiCp-T6jAE Mahon et al198 MVCjshear 01-980 0-24 ay UTS l12124-14SiCw-UAjOA Vasudevan et al201 MVCjshear 01-690 0-20 ay UTS [f

MB85-15SiCp-UAjOA Lewandowski MVC 01-300 0-08 (ly af (fet al189190

M B85-15SiCp-UAjOA Liu 195 MVC 01-300 0-08 ay (ff q6061AI-15AI203-UAjOA Liu et al194195197 MVC 01-300 0-11 ay af q Damage

quantification6090AI-25AI203-SAjT6 Lewandowski et al193 MVC 01-400 GfMB78-15SiCp-UAjOA Singh and MVC 01-500 q Damage

Lewandowski199 quantificationA356-1 Oj20SiCp- T6 Embury et al184 MVC 01-850 q Damage

quantificationAI-AI3Ni Zok 152 MVC 01-690 0-45 ay UTS lt1

Mg matrixAZ91-20SiCp-T4 Lewandowski et al193 01-350 0-12 GfAZ91-19SiCp15 llm-T6 Lewandowski et al193 MVC 01-440 0-14 ay UTS af [f Damage

quantificationAZ91-20SiCp52 llm-T6 Lewandowski et al193 MVC 01-490 0-19 ay UTS af [f Damage

quantificationCu matrixCu-28W Zok152 MVC 01-690 UTSq

IntermetallicsNiAI Margevicius and Transgranularj 01-1400 0-140 (ly (ff Gf wj

Lewandowski155161163 inte rg ra nul ar PrepressurisedNiAI Weaver et al166167 Prepressu risedNi3AI Zok et al152170 Intergranular 01-965 af GfAI3Ti Witczak and Varin 169 2000 ay af lof HV PrepressurisedAmorphous metalsPd Cu Si Davis and Kavesh323 Shear 01-690 0-047 af EfZr Ti Ni Cu Be Lewandowski et al324 Shear 01-650 0-035 af Ff

CeramicsAI203 Bridgman36 2350-2960 afB203 Bridgman3637 2350-2960 af Gf density changeLiF Hanafee and 01-1300 Dislocation velocity

Radcliffe 176MgO Weaver and Brittlejshear 01-1000 ay af Ff

Paterson 180181NaCI Bridgman36 2350-2960 af [f

CRSS critical resolved shear stress delam delamination dajdn crack propagation rate EI elongation HV Vickers hardness J J-integral MVC microvoidcoalescence UTS ultimate tensile strength

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152 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

and any pressure variation reported during the testin addition to the load and strain measurementtechniques reported by the various investigators onthe materials listed Table 2 provides a similar list ofinvestigations organised by the type of material (egmetal intermetallic composite) tested as well as bythe crystal structure (eg bcc fcc hcp) of the metalsunder investigation Included in Table 2 are thespecific properties measured by each of the investi-gators and any comments related to the failure modespresent References to the works in Tables 1 and 2are provided while the specific data summariesappear in subsequent figures In most of the studieswhere testing is conducted with superimposed hydro-static pressure the specimens have been coated orjacketed274 with some impervious membrane (egpolymer Cu shrink fit tubing etc) in order to preventingress of the pressure medium into any surfacecracks porosity etc274 The membrane utilised istypically very thin and does not contribute signifi-cantly to the load bearing area of the specimenFurthermore pressurisation of specimens shieldedwith such membranes in and of itself has not pro-duced changes to the subsequent flow stress obtainedat atmospheric pressure

1

-2-1

o~ 1cr

2

3 Yield surface plotted in principal stress spacefor fully dense isotropic and homogeneousmaterial335336

(2)

(4)

(5)

ka = 511 + 512 + S13

kc = 2S13 + 533

shear stresses developed owing to the differences incompressibility between the matrix and the secondphase128 The maximum shear stress [max at thematrixsecond phase interface has been separatelyestimated by Das and Radcliffe73 and Ashby et al337

for a spherical particle and is given by

3Gm ( Km -Kp )[max = K 3K + 4G pm p m

where Gm is the shear modulus of the matrix Km

and K the bulk moduli of the matrix and the sec-ond phase respectively and P the applied hydro-static pressure Dislocations are generated when[max reaches the nucleation stress for dislocationgeneration which can be theoretically predicted ordetermined experimen tally338

Another manner in which shear stresses are gener-ated in polycrystalline materials through the simpleapplication of hydrostatic pressure is through theanisotropy of elastic constants91128 Crystals of allsystems except the cubic system can change shapewhen subjected to hydrostatic pressure cubic crystalshave isotropic bulk moduli The volume compress-ibility which is the inverse of the bulk modulus isthe pressure induced change in volume of a crystalnormalised to its original volume and the linearcompressibility k is the amount of pressure inducedlength change in a straight line normalised to itsoriginal length For the cubic system k is independentof orientation and is related to the elastic compliance5ij through

k = 511 + S12 bull bull bullbull bull (3)For the trigonal hexagonal and tetragonal systemstwo constants are required the value in the a directionka and the value in the c direction kc These compress-ibilities are related to the elastic compliance 5ij by

Effects of superimposed pressure onstress state in cylindrical specimensConditions present before necking incylindrical specimensPlastic deformation in metallic systems tested at lowhomologous temperatures primarily occurs via dislo-cation generation andor movement via shear stressesoften referred to as conservative motion or glidePlastic deformation under such conditions occurswhen the effective stress (j equals the yield strengthin tension (Jy where the effective stress is given as

- 1 ( )2 ( )2 ( )2] 120=0[(J1-(J2 + 02-(J3 + (J3-(J1

(1)and (Jb (J2 and (J3 represent the principal stressesThe application of a purely hydrostatic stress (ie(J1 = 02 = (J3) produces no shear stress in a homo-geneous and isotropic material as shown by the 3-Dyield surface plotted in stress space in Fig 3 Ahydrostatic stress is represented as the axis of thecylinder in Fig 3 and since such stresses never touchthe yield surface there should be no effect ofpressurisationpressure soaking on the subsequentflow behaviour when uniaxial testing is conducted atatmospheric pressure Pressurisation in this casedenotes the simple application of hydrostatic pressureto a material and its subsequent removal Thereshould similarly be little effect of superimposed press-ure on yielding when testing is conducted on acylindrical specimen in the presence of a confining(ie hydrostatic) pressure as the stress state up to theultimate tensile stress (UTS) (ie before necking) insuch specimens consists of the uniaxial stress plusany superimposed hydrostatic pressure

However simple pressurisation can serve as ameans for generating dislocations in a materialaround inclusions and other defects as there are local

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 153

1

4 Yield surface plotted in principal stress spacefor material containing void fraction of a 0057and b 0180 (Ref 336)

1

1

a~l 05cr

o~ta

-05

-1

-1

(a)

(b)

The linear compressibility in any other direction kris given by

kr = ka + (ke - ka)r2 (6)

where r is the direction cosine with subject to thec axis

If non-cubic metals can change shape because ofpressurisation then a random aggregate of manycrystals when subjected to unit hydrostatic pressurewill develop shear stresses across grain boundaries Itis this shear stress which produces dislocation gener-ation in anisotropic materials

The degree of anisotropy in these non-cubic systemsis given in terms of the ratio keka The anisotropy ofa number of hexagonal metals is given in Table 3Those metals with a high degree of anisotropy Cdand Zn have been shown91339 to require only modestlevels of pressure ( 300 MPa) to induce plastic strainin the grains while metals with ratios close to one(where a cubic metal equals 10) Zr and Mg requiredthe highest pressures ( 2middot6 GPa) to produce onlytrace amounts of plastic deformation Although TEManalyses have confirmed the presence of pressureinduced dislocations around inclusions in less pureFe and Fe-C alloys containing inclusions65139 highpurity cubic metals such as Cu AI Fe and Ni haveshown no such plastic deformation after pressuris-ation to levels up to 1 GPa (Refs 109 339)

Porous materials consisting of either interconnectedor isolated pores are also highly pressure sensitive340provided the pressure medium is shielded from thespecimen to prevent ingress of the pressure medium(ie gas liquid) into the pores The 3-D yield loci forsuch materials are distinctly different from that shownin Fig 3 for homogeneous and isotropic materialsShown in Fig 4 are 3-D yield loci for porous materialscontaining increasing levels of porosity335336341342It is clear that the application of a hydrostatic pressureof sufficient magnitude in these cases can touch theyield surface and thereby produce plastic flowExamples of such effects are provided in works onporous Fe (Refs 62 137)

where Oflow is the flow stress a the minimum specimenradius R the radius of curvature at the neck or notchand rn the distance from the centre along the planeof the neck

Since the notchneck geometry will often changewith additional deformation the level of triaxialtensile stress resulting from deformation of such

International Materials Reviews 1998 Vol 43 NO4

mens) when subsequently tested in tension also experi-ence triaxial tensile stresses in the neckednotchedregion In this case the major difference between thenecked region which evolved during deformation andthat simulated by prenotching a pristine (ie non-deformed) specimen relates to the differences indeformation history (and any damage) present in thenecked region as compared to the notched regionBridgman provided an estimate of the additionalhydrostatic tension OT in the plane of a neck ornotch2436 as

Conditions present past necking incylindrical specimensOnce a neck begins to form in a cylindrical tensilespecimen tested at atmospheric pressure triaxialtensile stresses develop in the necked region Boththe magnitude and location of such triaxial stressesvary with location in the neck which develops withadditional deformation Prenecked (eg notched speci-

Table 3 Linear compressibility and anisotropyfactors for some non-cubic materials(Refs 128 339)

Lattice ratioLinear compressibility MPa

Metal cia c axis ke a axis ka Ratio keka

Cadmium 18856 1890 x 106 217 X 106 870Zinc 18564 1341 x 106 201 X 106 670Bismuth 26095 1645 x 106 684 X 106 240Magnesium 16235 1016 x 106 1016 X 106 1middot00Zirconium 1middot5931 380 x 106 3middot80 X 106 1middot00Titanium 15870 270 x 106 270 X 106 100Beryllium 15684 227 x 106 291 X 106 078

(a 12 )

OT = Oflow In 1 + 2R - 2a~ (7)

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154 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Superimposed Hydrostatic Pressure MPa

4340 tenlpered 3000C 152

4340 tempered (eQ 5000C 152

4340 tempered 7000C 152

o 4310-Lower Yield 133

bullbull 4330-Lower Yield 113

6 01 Tool Steel Hard 152

6 01 Tool Steel Mediunl 152

6 01 Tool Steel Soft 152

[S ri-V Steel 9500C FRT 152

fpound Ti-V Steel 700degC FRT 15~

bull 7075AI-T651(TR) 5051

bull 7075AI-T65 I(WR) 5051

T 7075AI-T65I (RW) 5051

() 201411 1(21)

EE BY -80 1ower Yield 134

bull Maraging-Unaged (Ten) 134

bull Maraging-Unaged (Comp) ]34

bull Maraging-Aged (Ten) 134

bull1200

(a)

bullbull

1000

EB

[SJ

800600400200

bull bull bull bullbullbullII bullbull JI bullbull Q bullbull bull

~ 6III II II bull

j 6 i i6

o

20

o

=~~ 15Q)~~

rJ)

0

~ 10~

e~ 05Z

~~ 1500

2000

=~eJ)

~ 1000~~

rJ)

e-Q)

~

00(b)

(gt 2124J() () I

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure

5 Effect of pressure on yield strength of various bee and fcc metallic alloys

specimens will vary past necking in the cylindricalspecimen Thus while the level of superimposedhydrostatic pressure has been kept relatively constantin many of the studies listed in Tables 1 and 2 thetriaxial stresses present in the neck during tests withsuperimposed pressure will depend on a variety offactors including the neck geometry level of superim-posed pressure and the flow stress of the materialIt is important to note that some studies investigat-ing the effects of superimposed pressure on tensiontests have been conducted under conditions suchthat compressive triaxial stresses were present in thenecked region In these cases the levels of superim-posed pressure were high enough to overcome thetriaxial tensile stresses which developed in the evolv-ing neck Thus the ability to monitor visually thedevelopment of the neck during tests with superim-posed pressure as described above or conductinginterrupted tests where the neck can be physicallymeasured outside of the high pressure environmenthas some merits858689103197213

Effects of superimposed pressure onflow behaviourEffects of superimposed pressure onyield stressFigures 5-8 summarise published data on the effectsof pressurisationpressure soaking as well as tensiletesting at different levels of superimposed hydrostaticpressure on the yield strength typically reported asthe 0middot2 offset yield strength In the former tests theyield strength was measured at atmospheric pressureafter pressurisation while the measurements of yieldstress in the latter cases occurred during tensile testsconducted with superimposed hydrostatic pressureThe pressure medium utilised in the studies summar-ised was either an oil medium or Ar gas and wasconfirmed to be hydrostatic Figure 5 summarisesdata obtained on a variety of steels and aluminiumalloys while Fig 6 shows similar data obtained on avariety of single phase metals possessing a bcc crystalstructure Figure 7 is a plot of the same type of

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 155

___bull __ Ar111co Iron 65

5b 6b 7b and 8b are plots of the ratio of the yieldstrength obtained at pressure (or after pressure soak-ing) to that of the control material (ie no pressuresoaking) in the manner utilised by a number ofinvestigators henceforth this is called the normalisedyield strength Pressure independent yielding is rep-resented by the horizontal line at 1middot0 for the normal-ised yield strength in Figs 5b-8b It is clear fromFig 5a that a number of conventional structuralmetallic alloys exhibit nominally pressure independ-ent yielding behaviour as predicted by equation (1)Slight positive deviations for monolithic materials (ienormalised yield strengthgt 1 in Fig 5b) have beenexplained as in part due to the pressure depend-ence of the shear modulus which though modestis non-zero for various metallic materials136Models313314 have been developed to predict suchpressure dependent yielding in metallic materials andmetallic glasses321-323 and a few studies have invokedsuch models to explain such pressure dependence ofthe yield stress136 It should be noted that there havebeen observations of materials which exhibit muchgreater positive deviations than those of the monolithicmetals summarised in Fig 5a and b For example ithas been clearly shown that superimposed pressuresignificantly inhibits dislocation mobility in LiFthereby elevating the flow stress above that obtainedat atmospheric pressure176

It is also clear that some of the monolithic metalsshown in Fig 5a and b as well as a variety of bccmetals (cf Fig 6a and b) and certain chemistries ofthe intermetallic NiAI shown in Fig7a and b ex-hibit a significant decrease in the yield strength afterpressure soaking or during tests conducted withsuperimposed pressure In these cases the materialstypically exhibited a yield point and Liiders exten-sion before pressure soaking or testing with superim-posed pressure Pressurisation (andor testing withpressure) was shown to remove the yield pointand Liiders strain and thereby reduce the yieldstrength155157159161162166167as illustrated for castextruded NiAI in Fig 7c As shown in Figs 6a andband 7a and b large reductions in yield strengthwere obtained in Fe (Refs 65 147) Cr (Refs 59 6466 72) and commercially pure NiAI (Refs 155 157161-163) that had been cast and extruded ExtensiveTEM analyses in these cases revealed that pressureinduced dislocation generation occurred at non-metallic inclusions and other inhomogeneities in thesematerials6465155157158161an example of which isshown in Fig 7d (Ref 157) The generation of thesemobile pressure induced dislocations thereby reducedthe yield strength while subsequent thermal agingstudies conducted for sufficient time-temperaturecombinations at atmospheric pressure enabled relock-ing of the dislocations by interstitial impurities (egC) and a return of the yield point and Liidersstrain6465107147166as illustrated for NiAI in Fig7c(Ref 159) Similar studies166167 conducted on highpurity NiAI failed to reveal a yield point and anysubsequent effect of pressurisation on the yield stressas shown in Fig 7a and b consistent with sucharguments Pressurisation of the largest grained Fein Fig 6a and b (Ref 147) to increasingly higherpressures eventually produced excessive generation

International Materials Reviews 1998 Vol 43 NO4

1200

(a)

(b)

---)

1000800600

~_-----1-~ - --

400200

- - Chromium 64

bull - Iodide Chromium 72

Superimposed Hydrostatic Pressure MPa

bull ~ ~- Y- -y_~~~ - - -9

-------

cOil 15cQJ

000 10~~5 050Z

000

800

eo 700~~ 600pound 500eiJcCJ 400V)

0 300~~ 200

100o

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

20

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

6 Effeet of pressure on yield strength of variousbee metals GS grain size

--0 Fc GS=11Jlnl 147

-0 Fe GS=14Jlm 147

-[S- Fe GS=19Jlm 147

-83- - Fe GS=30Jlm 147

-- - Fe GS=450~lIn 147

6 - - PM T 72- ungsten

-pound --Arc-Melted Tunsten 72

information for the intermetallic NiAI which possessesa B2 (ie bcc derivative) crystal structure while Fig 8is a plot of data from more recent work on compositesbased on either aluminium or magnesium alloymatrixes The data reported for the control materials(ie no pressure soaking) occur on the ordinate at0middot1 MPa (ie atmospheric pressure) Figures 5a 6a7a and 8a summarise the reported values for theyield strength obtained either during tension testswith superimposed pressure or after pressure soakingat the levels of hydrostatic pressure indicated Figures

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156 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullNill Cast and extruded 161

-[S)- - CP-NiAI Prepressurised 166

-EB - - - HP NAlP d 166- 1 repressunse

- -- - - - NiAI-NPrepressurised 166

50

300

(a)

1500

EB

(b)

middotmiddotlSI

__

middotEB

-bullbull-

bull

1000

-----------

1

500

_------------ --- -_---

Superimposed Hydrostatic Pressure MPa

100

50

20

00

o

c~ 15QJl-rj~ 10~8~ 05Z

oo 500 1000 1500

Superimposed Hydrostatic Pressure MPa

el~~ 200

250

o annealedp ~a~~a p ~a~~a p ~~~aT = 200degC 2h T = 400degC 2h

Strain

(c)d

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure c stress-strain curvesof polycrystalline NiAI tested in tension after annealing at 82JOC for 2 h pressurised to 14 GPa and tested at atmospheric pressure and afteraging pressurised specimens at either 200degC or 400degC for 2 h (Ref 159) (arrows show proportional limit) d dislocations being punched from Zrinclusion in NiAI pressurised to 1middot4 GPa (Refs 156 157 160 161)

7 Effect of pressure on yield strength of NiAI

of dislocations and a slight increase in the yieldstrength because of work hardening Little effect ofpressurisation was 0bserved on higher strengthPowder metallurgy produced NiAI (cf Fig7a

International Materials Reviews 1998 Vol 43 No4

and b)166 or W as well as arc-melted W (cf Fig6aand b) 72 in part due to the higher strengths of thematerials tested and the limited range of pressuresutilised

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 157

500

600(a)

Effects of pressure on work hardeningexponent nThe effects of testing with superimposed pressureon the work hardening exponent n have beeninfrequently studied Figure 9a and b illustrates theexperimentally measured effect of superimposed press-ure on n for a high strength aluminium alloy(7075- T651) tested in different orientations withrespect to the rolling direction Testing was conductedwith superimposed pressure on either uniaxial tensionspecimens or plane strain tension specimens andgenerally revealed an increase in n with increasingpressure The authors5051 indicated that such obser-vations could be related to the amount of secondphase particles which could punch out dislocationloops because of their smaller compressibility in amanner analogous to that described above for thecomposite materials

yield stress apparently arises because of pressureinduced dislocation generation around the reinforce-ment which increases significantly the local dislo-cation density thereby providing local hardening anda higher yield strength192195196 Transmission elec-tron microscope studies have confirmed that suchevents can occur provided the pressurisation is con-ducted at a large enough pressure to generate shearstresses of sufficient magnitude near the reinforce-ment192 Testing with superimposed pressure has alsobeen shown to inhibit the accumulation of damage(eg void initiation and growth) in such materials Asthe accumulation of damage reduces the load bearingarea and instantaneous modulus in such compositesand thereby reduces the strain hardening rate press-ure induced damage suppression has been proposedas also contributing to the elevated flow stressesobtained during tests conducted with superimposedpressure192196201 This point is further discussedbelow when summarising the effects of confiningpressure on the UTS In addition recent work hasalso shown that the level of residual stress in thematrix and reinforcement can be changed via pressur-isation343344 Finally various models315-320 have indi-cated that the presence of the non-deformingreinforcement particles provides constrained flow andenhances the flow stress of the matrix The super-position of pressure during tension testing shouldcounteract this effect as illustrated in a fewpapers318-320

15001000

== 0---

~ - - - ---= = = t0- -- - -

(b)

500Superimposed Hydrostatic Pressure MPa

oo

20

EZ 05-

- --6--- 2014AI-20SiCp 13 Jlm-AE 152201

-J - - 2014AI-20SiCp 13 Jlm-T6 152201

-1- - - 2124AI-14SiCw 1 Jlrn-UA 152201

-T---- 2124AI-14SiCw 1 ~m-OA 152201

-X - AI-AI Ni l~m 1523

0-- IIOOAJ-IOAI)O_~ 193

ltgt 193- -- 1100AI-15Al)0 -

- -0- - - 6061AI-15AJ 0 13lrn-UA 1952 3

-- -0- -- 6061AI-15AI 0 (13lm-OA 1952 3

- - -[SJ- - - 6061AI-15At) 0 13~ln-UA 185_ 3

- - -EB- - - 6090AI-25SiCp-SA 193

- - -- - - 6090AI-25SiCp-T6 193

-0- AZ91-19SiCp 15~lTn-T6 193

-e- AZ91-20SiCp52-lIn-T6 J93

c ~~~1-~ 200l x~ -X- X- y

100

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

8 Effect of pressure on yield strength ofdiscontinuously reinforced metal matrixcomposites

The largest changes in the yield strength obtainedeither after pressurisation or during tests with super-imposed pressure have been exhibited by compositematerials as shown in Fig 8a and b (Refs 152 185191-196 198 200 201) One source of the enhanced

Superimposed Hydrostatic Pressure MPa

00o 500 1000 1500 Effects of pressure on UTS

The experimental data for the UTS obtained viatension testing with a range of superimposed pressuresare provided for both monolithic metals as well ascomposites in Figs 10-15 As indicated above thestress state at the UTS (ie before necking) in suchspecimens consists of the uniaxial stress plus anysuperimposed hydrostatic pressure Data obtainedfrom some of Bridgmans original works are providedin Figs 10-13 for a variety of ferrous based systemsheat treated to different strength levels and micro-structures Figure 14a summarises similar data for avariety of other ferrous and non-ferrous structuralmaterials Figure 14b provides the ratio of the UTS

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158 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-6- _ TR uniaxialmiddotmiddotAmiddot TR plane strain-0 --- TW uniaxial

----e TW plane strain-0 - WRuniaxialbull - WRplanc strain

- --0 RW uniaxial- -+- - RW plane strain

-fSJ- Fe-034C-O75Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-045C-O83Mn-OO l6P-O035S-O19Si (as-received)

o normalised l650degF---0 annealed fine-grained- -6- annealed coarse-grained

- - - - - brine-quenchedtenlpered 600degF- - -+- - - brine-quenchedtempered 600degF-- -bull- - -- brine-quenchedtempered 900degF

015 3000

3000

middot11bull

1500 2000 25001000500Superimposed Hydrostatic Pressure MPa

o-- -0--

-6---e----+- -

--SJ-- Fe-O68C-O 7lMn-OO l3P-O025S-O19Si (as-received)

----0 --- Fe-O9C-O47Mn-O015P-O036S-OllSi (as-received)normalised 1650degFannealed fine-grainedannealed coarse-grainedbrine-quenchedspherodisedbrine-quenchedtempered 600degFbrine-quenchedtenlpered 900degF

bullbullbull

oo

2500

500

ce~E 1500rrJ~J 1000

10 Effect of pressure on UTS of various steelstested by Bridgman36

600

(a)

500 600

500

IImiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

middot0-middot -0

400

400

0

300

300

200

200

(b)

100

100Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

bullbull - A R bullbull

~ bull ~

000o

= 200Q)

=oc0lt

~ 150~=2

Q)C

100tt==~ 050eoZ 000

o

a n v hydrostatic pressure b normalised n v superimposedhydrostatic pressure

9 Effect of pressure on strain hardening exponentn of 7075AI- T651 (Refs 50 51)

3000

11 Effect of pressure on UTS of various steelstested by Bridgman36

Superimposed Hydrostatic Pressure MPa

500o

o -0

1500 2000 2500 30001000500

bullbull middot11II bull

~o Q ~omiddot omiddot

6 middot0middot omiddotmiddotmiddot=ltgt 6

1000

2500

ri1~ 1500J

~ 2000E

obtained at high pressure to that obtained at atmos-pheric pressure and a normalised UTS of 1middot0 indicatesno measurable effect of superimposed pressure onthe UTS The data for the monolithic metalsshown in Figs 10-13 as well as those summar-ised in Fig 14a and b indicate that superimposedpressure generally has a relatively minor effect on theUTS of most monolithic metals though someexceptions are shown Figure 15a and b illustratesthat composite materials often exhibit significantpressure dependent values for the UTS This hasbeen attributed152185189-201 to the pressure inducedsuppression of damage associated with the reinforce-ment and the matrix (eg void initiationgrowthcoalescence) which is covered in more detail in thefollowing sections on fracture behaviour

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 159

Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

A-+

bull -- -

0middot ------ -----()---6 - - - -

-8

iJII

-4-

-8-

---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

-8--- -lt)-

--

1000

5000

4000

C~ 3000~rJ5

2000 l-3~0

o S - - ~ lJS

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

I I I I I Iii I i

- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

3000

2500 -

d )000 f~~ -

~ 1500

~ middot_cmiddot- ~1000 ~_ibullbullbullbullbull~ - - -- - -- --0

s ti

500

12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure llPa

Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

- - -fr-

---]--

----T-

---0--

- - -lS -

------ - --(gt

--+-0-

4340 tempered 3000e 152

4340 tempered 5000e I 52

4340 tempered 7000e 152

01 Tool Steel Hard 152

01 Tool Steel Medium 152

01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

o 2124AI-14SiCw IJlm-UA 152201

bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

-+ Cu-28W 152

- - - -() - - - AI- Al Ni 152-

800

- - - -----------

~z~~~---~-----~bull-----~200

(a)

ts------6---1---------------- ------~

(b)

20

oo 100 WO ~O 400 ~O WO mo WO

Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

05

100

1000

1000

(a)

(b)

800

800600

600400

400

lZ91 19i

200

200Superimposed Hydrostatic Pressure MPa

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot-[H

----- ------0--middot- ----0

------6--- --6- ----------fJ--- --6

-----[S]----- ----[S]

-1-- - - - - - gtJ- - - - - - -Y- - -- - - -I- - - - - - gtJ

- -_~ ~~-~----- ~ _

middotmiddot~~-plusmn~middot~1middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

Superimposed Hydrostatic Pressure MPa

(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

~~ 1500

rJ5~ 1000

500

00

20

1500~~8 10l-o0Z

05

000

categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

References1 T von KARMAN Z Ver dt lng 19115517492 P W BRIDGMAN Proc Am Acad Arts Sci 1911 47 3473 P W BRIDGMAN Philos Mag 1912 24 634 P W BRIDGMAN Proc Am Acad Arts Sci 191449 6275 P W BRIDGMAN Phys Rev 1916 7 215

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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Mechanics Zurich 1926 53 1927 Zurich Orell Fiissli13 P w BRIDG~IAN Phys Rev 1927 29 18814 P W BRIDG~IA Proc Am Acad Arts Sci 192964 3915 P w BRIDG~[A Proc Am Acad Arts Sci 1931 66 25516 P w BRIDG~IA Proc Am Acad Art Sci 1933682717 P w BRIDG~IAN Phys Rev 1935 48 82518 P w BRIDG~[AN J Appl Phys 1937 8 32819 P w BRIDG~IAN Trans AIJvIE 1938 19 92220 P w BRIDG~IAN Jet Technol 1938 5 3221 P w BRIDG~IAN AJech Eng 193961 (2) 10722 P w BRIDG~IAN Pmc Am Acad Arts Sci 1940 74 123 P w BRIDG~IA Proc Am Acad Arts Sci 1940 74 1124 P w BRIDG~IAN Trans ASJvI 1944 32 55325 P w BRIDG~IAN Am Sci 1943 31 126 P w BRIDG~IAN in Colloid chemistry (ed J Alexander) 327

1944 New York Van Nostrand27 P w BRIDG~IAN JVIet Teclmol 1944 11 3228 P w BRIDG~IAN Rev lVIod Ph)s 1945 17 329 P W BRIDG~IAN J Appl Plzys 1946 17 69230 P w BRIDG~IAN J Appl Phys 1946 17 20131 P w BRIDG~IAN J Appl Plzys 1946 1722532 P w BRIDG~IAN J Appl Phys 1947 1824633 P w BRIDG~1AN in Fracturing of metals 240 1948 Cleveland

OH ASM34 P w BRIDG~IAN Research 1949 2 55035 P w BRIDG~IAN Endeavour 1951 106336 P W BRIDG~IAN Studies in large plastic flow and fracture -

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335 s M DORAIVELU H L GEGEL J S GUNASEKERA J C MALAS

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and magnesium for automotive applications (edJ D Bryant) 189 1996 Warrendale PA TMS-AIME

337 M F ASHBY S H GELLES and L E TANNER Phios Mag 196919 757

338 A H COTTRELL Theory of crystal dislocations 1964 NewYork Gordon and Breach

339 T E DAVIDSON J C UY and A P LEE Trans AIME 1965233820

340 J w SWEGLE J Appl Phys 1980 51 2574341 E J HILINSKI J J LEWANDOWSKI T J RODJOM and P T WANG

in 1994 World PM congress (ed C Lall et al) 259 1994Princeton NJ MPIF

342 E J HILINSKI 1 J LEWANDOWSKI T J RODJOM and P T WANG

in 1994 World PM congress (ed C Lall et al) 269 1994Princeton NJ MPIF

343 c LIU and J J LEWANDOWSKI Unpublished research CaseWestern Reserve University Cleveland OH 1991

344 c LIU G MICHAL and J J LEWANDOWSKI in Residual stressesin composites measurement modeling and effects on thermo-mechanical behavior (ed E V Barrera et al) 1993 DenverCO TMS

345 P F THOMASON Ductile fracture of metals 1990 New YorkPergamon Press

346 J F KNOTT Fundamentals of fracture mechanics 1973London Butterworths

347 A W THOMPSON and J F KNOTT Metall Trans A 199324A523

348 R O RITCHIE and A W THOMPSON Metall Trans A 198516A233

349 F A McCLINTOCK and A S ARGON Mechanical behaviour ofmaterials 1966 Reading MA Addison-Wesley

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 187

350 R O RITCHIE J F KNOTT and J R RICE J Mech Phys Solids1973 21 395

351 M F ASHBY J D EMBURY S H COOKSLEY and D TEIRLINCK

SCI Metall 1985 19 385352 M A MEYERS and K K CHAWLA Mechanical behavior of

materials 1998 Upper Saddle River NJ Prentice Hall353 A SAMANT and 1 1 LEWANDOWSKI Metall Mater Trans A

1997 28A 2297354 J1 LEWANDOWSKI and J F KNOTT in Proc 7th Int Conf on

Strength of metals and alloys - ICSMA 7 Montreal Aug1985 1193 1985 New York Pergamon Press

355 J R LOW in Relation of properties to microstructure 1631953 Novelty OH ASM

356 A N STROH Adv Phys 1957 6418357 A N STROH Phios Mag 1958 3 597358 1 FREIDEL Dislocations 1964 New York Pergamon Press359 1 F KNOTT and A H COTTRELL J Iron Steel Inst 1963

201249360 J F K~OTT J Iron Steel Inst 1966 204 104361 1 F KOTT J Iron Steel lISt 1966 204 1014362 J F K~OTT J Iron Steel Inst 1967 205 288363 OROWAN Trans Inst Eng Shipbuilders Scotland 194589 1165364 N N DAVIDENKOV Dinamicheskaya ispytania metallov 1936

Moscow USSR365 1 1 LEWANDOWSKI and A W THOMPSON Metall Trans 1986

17A 1769366 J J LEWANDOWSKI and A W THOMPSON Acta Metall 1987

35 1453367 A SAMANT and 1 J LEWANDOWSKI Metall Mater Trans A

1997 28A 389368 D TEIRLINCK F ZOK J D EMBURY and M F ASHBY Acta

Metall 1988 36 1213369 D TEIRLINCK M F ASHBY and J D EMBURY in Advances in

fracture research - ICF 6 New Delhi India Dec 1984 105New York Pergamon Press

370 w M GARRISON Jr and N R MOODY J Phys Chem Solids1987 48 1035

371 A W THOMPSON Metall Trans A 1987 18A 1877372 L M BROWN and J D EMBURY in Proc 3rd Int Conf on

Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

374 s H GOOD and L M BROWN Acta Metall 197927 1375 L M BROWN and w M STOBBS Phios Mag 197634 351376 P F THOMASON Ductile fracture of metals 94 1990 New

York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 151

Table 2 (cant)

Pressure range

Materials Researcher(s) Failure mode P MPa Pj(fy Measured properties Note

Metalsbee metalsNb Bridgman36 01-2850 (ff qTa Bridgman36 01-2850 (ff [f

Ta Nishihara et al114 01-500 ayUTS rof Temperature upto 600C

Ta Robbins and Wronski131 1500 (fy Prepressu rised0-500

W Bridgman36 01-2840 af lofW Das and Radcliffe73 01-1100 0-15 (ff af lofW Daga71 01-1100 0-20 ay (ff qW Davidson et al74 CleavageMVCjshear 01-1600 qW Mellor and Wronski108 2800 (fy af EI Prepressu rised

prestrainedhcp metalsBe (PM) Aladag45 Intergranularj 01-980 af [f

Aldag et al46 transgranularBe (PM) Andrews and 01-2700 Prepressurised

Radcliffe49Be (ingot) Aladag45 Transgranular 01-980 0-38 (fy af [f

Aldag et al46

Be (castrolled) Bedere et al55 Intergranularj 01-1500 0-122 (ly af [f

transgranular shearCd Nakajima et al111 01-600 ayCo Davidson et al74 CleavagejMVCjshear 01-2350 f~Mg Davidson et aJ74 MVCjshear 01-1800 4Mg Pugh and Green 123 01-460 [fAZ91 (PM) Lahaie et al101 Intergranularshear 01-690 0-22 (fy ltofAZ91-T4jT6 Lewandowski et al193 01-380 af (f

Zn Davidson et al74 Brittlejplastic rupture qZn Pugh and Green 123 Cleavageplastic 01-138 ay q

ruptureZn-41AI Pugh and Green 123 01-410 ltofTi-7 AI-2Nb-1Ta (x) Johnson et al97 172 02 ay af lt1 Prepressu risedTi-6AI-4V (ajm Johnson et al97 172 02 (fy (ff Gf Prepressu risedTi-13V-l1 Cr-3AI (x) Johnson et al97 172 0middot2 ay af q Prepressurised

Metal matrix composites

AI matrix2014-20SiCp-T6jAE ZOk152 MVCshear 01-980 0-24 ay UTS Gf

2124-14SiCw-UAjOA ZOk152 MVCshear 01-690 0-20 ay UTS l12014-20SiCp-T6jAE Mahon et al198 MVCjshear 01-980 0-24 ay UTS l12124-14SiCw-UAjOA Vasudevan et al201 MVCjshear 01-690 0-20 ay UTS [f

MB85-15SiCp-UAjOA Lewandowski MVC 01-300 0-08 (ly af (fet al189190

M B85-15SiCp-UAjOA Liu 195 MVC 01-300 0-08 ay (ff q6061AI-15AI203-UAjOA Liu et al194195197 MVC 01-300 0-11 ay af q Damage

quantification6090AI-25AI203-SAjT6 Lewandowski et al193 MVC 01-400 GfMB78-15SiCp-UAjOA Singh and MVC 01-500 q Damage

Lewandowski199 quantificationA356-1 Oj20SiCp- T6 Embury et al184 MVC 01-850 q Damage

quantificationAI-AI3Ni Zok 152 MVC 01-690 0-45 ay UTS lt1

Mg matrixAZ91-20SiCp-T4 Lewandowski et al193 01-350 0-12 GfAZ91-19SiCp15 llm-T6 Lewandowski et al193 MVC 01-440 0-14 ay UTS af [f Damage

quantificationAZ91-20SiCp52 llm-T6 Lewandowski et al193 MVC 01-490 0-19 ay UTS af [f Damage

quantificationCu matrixCu-28W Zok152 MVC 01-690 UTSq

IntermetallicsNiAI Margevicius and Transgranularj 01-1400 0-140 (ly (ff Gf wj

Lewandowski155161163 inte rg ra nul ar PrepressurisedNiAI Weaver et al166167 Prepressu risedNi3AI Zok et al152170 Intergranular 01-965 af GfAI3Ti Witczak and Varin 169 2000 ay af lof HV PrepressurisedAmorphous metalsPd Cu Si Davis and Kavesh323 Shear 01-690 0-047 af EfZr Ti Ni Cu Be Lewandowski et al324 Shear 01-650 0-035 af Ff

CeramicsAI203 Bridgman36 2350-2960 afB203 Bridgman3637 2350-2960 af Gf density changeLiF Hanafee and 01-1300 Dislocation velocity

Radcliffe 176MgO Weaver and Brittlejshear 01-1000 ay af Ff

Paterson 180181NaCI Bridgman36 2350-2960 af [f

CRSS critical resolved shear stress delam delamination dajdn crack propagation rate EI elongation HV Vickers hardness J J-integral MVC microvoidcoalescence UTS ultimate tensile strength

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152 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

and any pressure variation reported during the testin addition to the load and strain measurementtechniques reported by the various investigators onthe materials listed Table 2 provides a similar list ofinvestigations organised by the type of material (egmetal intermetallic composite) tested as well as bythe crystal structure (eg bcc fcc hcp) of the metalsunder investigation Included in Table 2 are thespecific properties measured by each of the investi-gators and any comments related to the failure modespresent References to the works in Tables 1 and 2are provided while the specific data summariesappear in subsequent figures In most of the studieswhere testing is conducted with superimposed hydro-static pressure the specimens have been coated orjacketed274 with some impervious membrane (egpolymer Cu shrink fit tubing etc) in order to preventingress of the pressure medium into any surfacecracks porosity etc274 The membrane utilised istypically very thin and does not contribute signifi-cantly to the load bearing area of the specimenFurthermore pressurisation of specimens shieldedwith such membranes in and of itself has not pro-duced changes to the subsequent flow stress obtainedat atmospheric pressure

1

-2-1

o~ 1cr

2

3 Yield surface plotted in principal stress spacefor fully dense isotropic and homogeneousmaterial335336

(2)

(4)

(5)

ka = 511 + 512 + S13

kc = 2S13 + 533

shear stresses developed owing to the differences incompressibility between the matrix and the secondphase128 The maximum shear stress [max at thematrixsecond phase interface has been separatelyestimated by Das and Radcliffe73 and Ashby et al337

for a spherical particle and is given by

3Gm ( Km -Kp )[max = K 3K + 4G pm p m

where Gm is the shear modulus of the matrix Km

and K the bulk moduli of the matrix and the sec-ond phase respectively and P the applied hydro-static pressure Dislocations are generated when[max reaches the nucleation stress for dislocationgeneration which can be theoretically predicted ordetermined experimen tally338

Another manner in which shear stresses are gener-ated in polycrystalline materials through the simpleapplication of hydrostatic pressure is through theanisotropy of elastic constants91128 Crystals of allsystems except the cubic system can change shapewhen subjected to hydrostatic pressure cubic crystalshave isotropic bulk moduli The volume compress-ibility which is the inverse of the bulk modulus isthe pressure induced change in volume of a crystalnormalised to its original volume and the linearcompressibility k is the amount of pressure inducedlength change in a straight line normalised to itsoriginal length For the cubic system k is independentof orientation and is related to the elastic compliance5ij through

k = 511 + S12 bull bull bullbull bull (3)For the trigonal hexagonal and tetragonal systemstwo constants are required the value in the a directionka and the value in the c direction kc These compress-ibilities are related to the elastic compliance 5ij by

Effects of superimposed pressure onstress state in cylindrical specimensConditions present before necking incylindrical specimensPlastic deformation in metallic systems tested at lowhomologous temperatures primarily occurs via dislo-cation generation andor movement via shear stressesoften referred to as conservative motion or glidePlastic deformation under such conditions occurswhen the effective stress (j equals the yield strengthin tension (Jy where the effective stress is given as

- 1 ( )2 ( )2 ( )2] 120=0[(J1-(J2 + 02-(J3 + (J3-(J1

(1)and (Jb (J2 and (J3 represent the principal stressesThe application of a purely hydrostatic stress (ie(J1 = 02 = (J3) produces no shear stress in a homo-geneous and isotropic material as shown by the 3-Dyield surface plotted in stress space in Fig 3 Ahydrostatic stress is represented as the axis of thecylinder in Fig 3 and since such stresses never touchthe yield surface there should be no effect ofpressurisationpressure soaking on the subsequentflow behaviour when uniaxial testing is conducted atatmospheric pressure Pressurisation in this casedenotes the simple application of hydrostatic pressureto a material and its subsequent removal Thereshould similarly be little effect of superimposed press-ure on yielding when testing is conducted on acylindrical specimen in the presence of a confining(ie hydrostatic) pressure as the stress state up to theultimate tensile stress (UTS) (ie before necking) insuch specimens consists of the uniaxial stress plusany superimposed hydrostatic pressure

However simple pressurisation can serve as ameans for generating dislocations in a materialaround inclusions and other defects as there are local

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 153

1

4 Yield surface plotted in principal stress spacefor material containing void fraction of a 0057and b 0180 (Ref 336)

1

1

a~l 05cr

o~ta

-05

-1

-1

(a)

(b)

The linear compressibility in any other direction kris given by

kr = ka + (ke - ka)r2 (6)

where r is the direction cosine with subject to thec axis

If non-cubic metals can change shape because ofpressurisation then a random aggregate of manycrystals when subjected to unit hydrostatic pressurewill develop shear stresses across grain boundaries Itis this shear stress which produces dislocation gener-ation in anisotropic materials

The degree of anisotropy in these non-cubic systemsis given in terms of the ratio keka The anisotropy ofa number of hexagonal metals is given in Table 3Those metals with a high degree of anisotropy Cdand Zn have been shown91339 to require only modestlevels of pressure ( 300 MPa) to induce plastic strainin the grains while metals with ratios close to one(where a cubic metal equals 10) Zr and Mg requiredthe highest pressures ( 2middot6 GPa) to produce onlytrace amounts of plastic deformation Although TEManalyses have confirmed the presence of pressureinduced dislocations around inclusions in less pureFe and Fe-C alloys containing inclusions65139 highpurity cubic metals such as Cu AI Fe and Ni haveshown no such plastic deformation after pressuris-ation to levels up to 1 GPa (Refs 109 339)

Porous materials consisting of either interconnectedor isolated pores are also highly pressure sensitive340provided the pressure medium is shielded from thespecimen to prevent ingress of the pressure medium(ie gas liquid) into the pores The 3-D yield loci forsuch materials are distinctly different from that shownin Fig 3 for homogeneous and isotropic materialsShown in Fig 4 are 3-D yield loci for porous materialscontaining increasing levels of porosity335336341342It is clear that the application of a hydrostatic pressureof sufficient magnitude in these cases can touch theyield surface and thereby produce plastic flowExamples of such effects are provided in works onporous Fe (Refs 62 137)

where Oflow is the flow stress a the minimum specimenradius R the radius of curvature at the neck or notchand rn the distance from the centre along the planeof the neck

Since the notchneck geometry will often changewith additional deformation the level of triaxialtensile stress resulting from deformation of such

International Materials Reviews 1998 Vol 43 NO4

mens) when subsequently tested in tension also experi-ence triaxial tensile stresses in the neckednotchedregion In this case the major difference between thenecked region which evolved during deformation andthat simulated by prenotching a pristine (ie non-deformed) specimen relates to the differences indeformation history (and any damage) present in thenecked region as compared to the notched regionBridgman provided an estimate of the additionalhydrostatic tension OT in the plane of a neck ornotch2436 as

Conditions present past necking incylindrical specimensOnce a neck begins to form in a cylindrical tensilespecimen tested at atmospheric pressure triaxialtensile stresses develop in the necked region Boththe magnitude and location of such triaxial stressesvary with location in the neck which develops withadditional deformation Prenecked (eg notched speci-

Table 3 Linear compressibility and anisotropyfactors for some non-cubic materials(Refs 128 339)

Lattice ratioLinear compressibility MPa

Metal cia c axis ke a axis ka Ratio keka

Cadmium 18856 1890 x 106 217 X 106 870Zinc 18564 1341 x 106 201 X 106 670Bismuth 26095 1645 x 106 684 X 106 240Magnesium 16235 1016 x 106 1016 X 106 1middot00Zirconium 1middot5931 380 x 106 3middot80 X 106 1middot00Titanium 15870 270 x 106 270 X 106 100Beryllium 15684 227 x 106 291 X 106 078

(a 12 )

OT = Oflow In 1 + 2R - 2a~ (7)

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154 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Superimposed Hydrostatic Pressure MPa

4340 tenlpered 3000C 152

4340 tempered (eQ 5000C 152

4340 tempered 7000C 152

o 4310-Lower Yield 133

bullbull 4330-Lower Yield 113

6 01 Tool Steel Hard 152

6 01 Tool Steel Mediunl 152

6 01 Tool Steel Soft 152

[S ri-V Steel 9500C FRT 152

fpound Ti-V Steel 700degC FRT 15~

bull 7075AI-T651(TR) 5051

bull 7075AI-T65 I(WR) 5051

T 7075AI-T65I (RW) 5051

() 201411 1(21)

EE BY -80 1ower Yield 134

bull Maraging-Unaged (Ten) 134

bull Maraging-Unaged (Comp) ]34

bull Maraging-Aged (Ten) 134

bull1200

(a)

bullbull

1000

EB

[SJ

800600400200

bull bull bull bullbullbullII bullbull JI bullbull Q bullbull bull

~ 6III II II bull

j 6 i i6

o

20

o

=~~ 15Q)~~

rJ)

0

~ 10~

e~ 05Z

~~ 1500

2000

=~eJ)

~ 1000~~

rJ)

e-Q)

~

00(b)

(gt 2124J() () I

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure

5 Effect of pressure on yield strength of various bee and fcc metallic alloys

specimens will vary past necking in the cylindricalspecimen Thus while the level of superimposedhydrostatic pressure has been kept relatively constantin many of the studies listed in Tables 1 and 2 thetriaxial stresses present in the neck during tests withsuperimposed pressure will depend on a variety offactors including the neck geometry level of superim-posed pressure and the flow stress of the materialIt is important to note that some studies investigat-ing the effects of superimposed pressure on tensiontests have been conducted under conditions suchthat compressive triaxial stresses were present in thenecked region In these cases the levels of superim-posed pressure were high enough to overcome thetriaxial tensile stresses which developed in the evolv-ing neck Thus the ability to monitor visually thedevelopment of the neck during tests with superim-posed pressure as described above or conductinginterrupted tests where the neck can be physicallymeasured outside of the high pressure environmenthas some merits858689103197213

Effects of superimposed pressure onflow behaviourEffects of superimposed pressure onyield stressFigures 5-8 summarise published data on the effectsof pressurisationpressure soaking as well as tensiletesting at different levels of superimposed hydrostaticpressure on the yield strength typically reported asthe 0middot2 offset yield strength In the former tests theyield strength was measured at atmospheric pressureafter pressurisation while the measurements of yieldstress in the latter cases occurred during tensile testsconducted with superimposed hydrostatic pressureThe pressure medium utilised in the studies summar-ised was either an oil medium or Ar gas and wasconfirmed to be hydrostatic Figure 5 summarisesdata obtained on a variety of steels and aluminiumalloys while Fig 6 shows similar data obtained on avariety of single phase metals possessing a bcc crystalstructure Figure 7 is a plot of the same type of

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 155

___bull __ Ar111co Iron 65

5b 6b 7b and 8b are plots of the ratio of the yieldstrength obtained at pressure (or after pressure soak-ing) to that of the control material (ie no pressuresoaking) in the manner utilised by a number ofinvestigators henceforth this is called the normalisedyield strength Pressure independent yielding is rep-resented by the horizontal line at 1middot0 for the normal-ised yield strength in Figs 5b-8b It is clear fromFig 5a that a number of conventional structuralmetallic alloys exhibit nominally pressure independ-ent yielding behaviour as predicted by equation (1)Slight positive deviations for monolithic materials (ienormalised yield strengthgt 1 in Fig 5b) have beenexplained as in part due to the pressure depend-ence of the shear modulus which though modestis non-zero for various metallic materials136Models313314 have been developed to predict suchpressure dependent yielding in metallic materials andmetallic glasses321-323 and a few studies have invokedsuch models to explain such pressure dependence ofthe yield stress136 It should be noted that there havebeen observations of materials which exhibit muchgreater positive deviations than those of the monolithicmetals summarised in Fig 5a and b For example ithas been clearly shown that superimposed pressuresignificantly inhibits dislocation mobility in LiFthereby elevating the flow stress above that obtainedat atmospheric pressure176

It is also clear that some of the monolithic metalsshown in Fig 5a and b as well as a variety of bccmetals (cf Fig 6a and b) and certain chemistries ofthe intermetallic NiAI shown in Fig7a and b ex-hibit a significant decrease in the yield strength afterpressure soaking or during tests conducted withsuperimposed pressure In these cases the materialstypically exhibited a yield point and Liiders exten-sion before pressure soaking or testing with superim-posed pressure Pressurisation (andor testing withpressure) was shown to remove the yield pointand Liiders strain and thereby reduce the yieldstrength155157159161162166167as illustrated for castextruded NiAI in Fig 7c As shown in Figs 6a andband 7a and b large reductions in yield strengthwere obtained in Fe (Refs 65 147) Cr (Refs 59 6466 72) and commercially pure NiAI (Refs 155 157161-163) that had been cast and extruded ExtensiveTEM analyses in these cases revealed that pressureinduced dislocation generation occurred at non-metallic inclusions and other inhomogeneities in thesematerials6465155157158161an example of which isshown in Fig 7d (Ref 157) The generation of thesemobile pressure induced dislocations thereby reducedthe yield strength while subsequent thermal agingstudies conducted for sufficient time-temperaturecombinations at atmospheric pressure enabled relock-ing of the dislocations by interstitial impurities (egC) and a return of the yield point and Liidersstrain6465107147166as illustrated for NiAI in Fig7c(Ref 159) Similar studies166167 conducted on highpurity NiAI failed to reveal a yield point and anysubsequent effect of pressurisation on the yield stressas shown in Fig 7a and b consistent with sucharguments Pressurisation of the largest grained Fein Fig 6a and b (Ref 147) to increasingly higherpressures eventually produced excessive generation

International Materials Reviews 1998 Vol 43 NO4

1200

(a)

(b)

---)

1000800600

~_-----1-~ - --

400200

- - Chromium 64

bull - Iodide Chromium 72

Superimposed Hydrostatic Pressure MPa

bull ~ ~- Y- -y_~~~ - - -9

-------

cOil 15cQJ

000 10~~5 050Z

000

800

eo 700~~ 600pound 500eiJcCJ 400V)

0 300~~ 200

100o

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

20

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

6 Effeet of pressure on yield strength of variousbee metals GS grain size

--0 Fc GS=11Jlnl 147

-0 Fe GS=14Jlm 147

-[S- Fe GS=19Jlm 147

-83- - Fe GS=30Jlm 147

-- - Fe GS=450~lIn 147

6 - - PM T 72- ungsten

-pound --Arc-Melted Tunsten 72

information for the intermetallic NiAI which possessesa B2 (ie bcc derivative) crystal structure while Fig 8is a plot of data from more recent work on compositesbased on either aluminium or magnesium alloymatrixes The data reported for the control materials(ie no pressure soaking) occur on the ordinate at0middot1 MPa (ie atmospheric pressure) Figures 5a 6a7a and 8a summarise the reported values for theyield strength obtained either during tension testswith superimposed pressure or after pressure soakingat the levels of hydrostatic pressure indicated Figures

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156 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullNill Cast and extruded 161

-[S)- - CP-NiAI Prepressurised 166

-EB - - - HP NAlP d 166- 1 repressunse

- -- - - - NiAI-NPrepressurised 166

50

300

(a)

1500

EB

(b)

middotmiddotlSI

__

middotEB

-bullbull-

bull

1000

-----------

1

500

_------------ --- -_---

Superimposed Hydrostatic Pressure MPa

100

50

20

00

o

c~ 15QJl-rj~ 10~8~ 05Z

oo 500 1000 1500

Superimposed Hydrostatic Pressure MPa

el~~ 200

250

o annealedp ~a~~a p ~a~~a p ~~~aT = 200degC 2h T = 400degC 2h

Strain

(c)d

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure c stress-strain curvesof polycrystalline NiAI tested in tension after annealing at 82JOC for 2 h pressurised to 14 GPa and tested at atmospheric pressure and afteraging pressurised specimens at either 200degC or 400degC for 2 h (Ref 159) (arrows show proportional limit) d dislocations being punched from Zrinclusion in NiAI pressurised to 1middot4 GPa (Refs 156 157 160 161)

7 Effect of pressure on yield strength of NiAI

of dislocations and a slight increase in the yieldstrength because of work hardening Little effect ofpressurisation was 0bserved on higher strengthPowder metallurgy produced NiAI (cf Fig7a

International Materials Reviews 1998 Vol 43 No4

and b)166 or W as well as arc-melted W (cf Fig6aand b) 72 in part due to the higher strengths of thematerials tested and the limited range of pressuresutilised

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 157

500

600(a)

Effects of pressure on work hardeningexponent nThe effects of testing with superimposed pressureon the work hardening exponent n have beeninfrequently studied Figure 9a and b illustrates theexperimentally measured effect of superimposed press-ure on n for a high strength aluminium alloy(7075- T651) tested in different orientations withrespect to the rolling direction Testing was conductedwith superimposed pressure on either uniaxial tensionspecimens or plane strain tension specimens andgenerally revealed an increase in n with increasingpressure The authors5051 indicated that such obser-vations could be related to the amount of secondphase particles which could punch out dislocationloops because of their smaller compressibility in amanner analogous to that described above for thecomposite materials

yield stress apparently arises because of pressureinduced dislocation generation around the reinforce-ment which increases significantly the local dislo-cation density thereby providing local hardening anda higher yield strength192195196 Transmission elec-tron microscope studies have confirmed that suchevents can occur provided the pressurisation is con-ducted at a large enough pressure to generate shearstresses of sufficient magnitude near the reinforce-ment192 Testing with superimposed pressure has alsobeen shown to inhibit the accumulation of damage(eg void initiation and growth) in such materials Asthe accumulation of damage reduces the load bearingarea and instantaneous modulus in such compositesand thereby reduces the strain hardening rate press-ure induced damage suppression has been proposedas also contributing to the elevated flow stressesobtained during tests conducted with superimposedpressure192196201 This point is further discussedbelow when summarising the effects of confiningpressure on the UTS In addition recent work hasalso shown that the level of residual stress in thematrix and reinforcement can be changed via pressur-isation343344 Finally various models315-320 have indi-cated that the presence of the non-deformingreinforcement particles provides constrained flow andenhances the flow stress of the matrix The super-position of pressure during tension testing shouldcounteract this effect as illustrated in a fewpapers318-320

15001000

== 0---

~ - - - ---= = = t0- -- - -

(b)

500Superimposed Hydrostatic Pressure MPa

oo

20

EZ 05-

- --6--- 2014AI-20SiCp 13 Jlm-AE 152201

-J - - 2014AI-20SiCp 13 Jlm-T6 152201

-1- - - 2124AI-14SiCw 1 Jlrn-UA 152201

-T---- 2124AI-14SiCw 1 ~m-OA 152201

-X - AI-AI Ni l~m 1523

0-- IIOOAJ-IOAI)O_~ 193

ltgt 193- -- 1100AI-15Al)0 -

- -0- - - 6061AI-15AJ 0 13lrn-UA 1952 3

-- -0- -- 6061AI-15AI 0 (13lm-OA 1952 3

- - -[SJ- - - 6061AI-15At) 0 13~ln-UA 185_ 3

- - -EB- - - 6090AI-25SiCp-SA 193

- - -- - - 6090AI-25SiCp-T6 193

-0- AZ91-19SiCp 15~lTn-T6 193

-e- AZ91-20SiCp52-lIn-T6 J93

c ~~~1-~ 200l x~ -X- X- y

100

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

8 Effect of pressure on yield strength ofdiscontinuously reinforced metal matrixcomposites

The largest changes in the yield strength obtainedeither after pressurisation or during tests with super-imposed pressure have been exhibited by compositematerials as shown in Fig 8a and b (Refs 152 185191-196 198 200 201) One source of the enhanced

Superimposed Hydrostatic Pressure MPa

00o 500 1000 1500 Effects of pressure on UTS

The experimental data for the UTS obtained viatension testing with a range of superimposed pressuresare provided for both monolithic metals as well ascomposites in Figs 10-15 As indicated above thestress state at the UTS (ie before necking) in suchspecimens consists of the uniaxial stress plus anysuperimposed hydrostatic pressure Data obtainedfrom some of Bridgmans original works are providedin Figs 10-13 for a variety of ferrous based systemsheat treated to different strength levels and micro-structures Figure 14a summarises similar data for avariety of other ferrous and non-ferrous structuralmaterials Figure 14b provides the ratio of the UTS

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158 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-6- _ TR uniaxialmiddotmiddotAmiddot TR plane strain-0 --- TW uniaxial

----e TW plane strain-0 - WRuniaxialbull - WRplanc strain

- --0 RW uniaxial- -+- - RW plane strain

-fSJ- Fe-034C-O75Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-045C-O83Mn-OO l6P-O035S-O19Si (as-received)

o normalised l650degF---0 annealed fine-grained- -6- annealed coarse-grained

- - - - - brine-quenchedtenlpered 600degF- - -+- - - brine-quenchedtempered 600degF-- -bull- - -- brine-quenchedtempered 900degF

015 3000

3000

middot11bull

1500 2000 25001000500Superimposed Hydrostatic Pressure MPa

o-- -0--

-6---e----+- -

--SJ-- Fe-O68C-O 7lMn-OO l3P-O025S-O19Si (as-received)

----0 --- Fe-O9C-O47Mn-O015P-O036S-OllSi (as-received)normalised 1650degFannealed fine-grainedannealed coarse-grainedbrine-quenchedspherodisedbrine-quenchedtempered 600degFbrine-quenchedtenlpered 900degF

bullbullbull

oo

2500

500

ce~E 1500rrJ~J 1000

10 Effect of pressure on UTS of various steelstested by Bridgman36

600

(a)

500 600

500

IImiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

middot0-middot -0

400

400

0

300

300

200

200

(b)

100

100Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

bullbull - A R bullbull

~ bull ~

000o

= 200Q)

=oc0lt

~ 150~=2

Q)C

100tt==~ 050eoZ 000

o

a n v hydrostatic pressure b normalised n v superimposedhydrostatic pressure

9 Effect of pressure on strain hardening exponentn of 7075AI- T651 (Refs 50 51)

3000

11 Effect of pressure on UTS of various steelstested by Bridgman36

Superimposed Hydrostatic Pressure MPa

500o

o -0

1500 2000 2500 30001000500

bullbull middot11II bull

~o Q ~omiddot omiddot

6 middot0middot omiddotmiddotmiddot=ltgt 6

1000

2500

ri1~ 1500J

~ 2000E

obtained at high pressure to that obtained at atmos-pheric pressure and a normalised UTS of 1middot0 indicatesno measurable effect of superimposed pressure onthe UTS The data for the monolithic metalsshown in Figs 10-13 as well as those summar-ised in Fig 14a and b indicate that superimposedpressure generally has a relatively minor effect on theUTS of most monolithic metals though someexceptions are shown Figure 15a and b illustratesthat composite materials often exhibit significantpressure dependent values for the UTS This hasbeen attributed152185189-201 to the pressure inducedsuppression of damage associated with the reinforce-ment and the matrix (eg void initiationgrowthcoalescence) which is covered in more detail in thefollowing sections on fracture behaviour

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 159

Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

A-+

bull -- -

0middot ------ -----()---6 - - - -

-8

iJII

-4-

-8-

---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

-8--- -lt)-

--

1000

5000

4000

C~ 3000~rJ5

2000 l-3~0

o S - - ~ lJS

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

I I I I I Iii I i

- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

3000

2500 -

d )000 f~~ -

~ 1500

~ middot_cmiddot- ~1000 ~_ibullbullbullbullbull~ - - -- - -- --0

s ti

500

12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure llPa

Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

- - -fr-

---]--

----T-

---0--

- - -lS -

------ - --(gt

--+-0-

4340 tempered 3000e 152

4340 tempered 5000e I 52

4340 tempered 7000e 152

01 Tool Steel Hard 152

01 Tool Steel Medium 152

01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

o 2124AI-14SiCw IJlm-UA 152201

bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

-+ Cu-28W 152

- - - -() - - - AI- Al Ni 152-

800

- - - -----------

~z~~~---~-----~bull-----~200

(a)

ts------6---1---------------- ------~

(b)

20

oo 100 WO ~O 400 ~O WO mo WO

Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

05

100

1000

1000

(a)

(b)

800

800600

600400

400

lZ91 19i

200

200Superimposed Hydrostatic Pressure MPa

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot-[H

----- ------0--middot- ----0

------6--- --6- ----------fJ--- --6

-----[S]----- ----[S]

-1-- - - - - - gtJ- - - - - - -Y- - -- - - -I- - - - - - gtJ

- -_~ ~~-~----- ~ _

middotmiddot~~-plusmn~middot~1middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

Superimposed Hydrostatic Pressure MPa

(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

~~ 1500

rJ5~ 1000

500

00

20

1500~~8 10l-o0Z

05

000

categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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152 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

and any pressure variation reported during the testin addition to the load and strain measurementtechniques reported by the various investigators onthe materials listed Table 2 provides a similar list ofinvestigations organised by the type of material (egmetal intermetallic composite) tested as well as bythe crystal structure (eg bcc fcc hcp) of the metalsunder investigation Included in Table 2 are thespecific properties measured by each of the investi-gators and any comments related to the failure modespresent References to the works in Tables 1 and 2are provided while the specific data summariesappear in subsequent figures In most of the studieswhere testing is conducted with superimposed hydro-static pressure the specimens have been coated orjacketed274 with some impervious membrane (egpolymer Cu shrink fit tubing etc) in order to preventingress of the pressure medium into any surfacecracks porosity etc274 The membrane utilised istypically very thin and does not contribute signifi-cantly to the load bearing area of the specimenFurthermore pressurisation of specimens shieldedwith such membranes in and of itself has not pro-duced changes to the subsequent flow stress obtainedat atmospheric pressure

1

-2-1

o~ 1cr

2

3 Yield surface plotted in principal stress spacefor fully dense isotropic and homogeneousmaterial335336

(2)

(4)

(5)

ka = 511 + 512 + S13

kc = 2S13 + 533

shear stresses developed owing to the differences incompressibility between the matrix and the secondphase128 The maximum shear stress [max at thematrixsecond phase interface has been separatelyestimated by Das and Radcliffe73 and Ashby et al337

for a spherical particle and is given by

3Gm ( Km -Kp )[max = K 3K + 4G pm p m

where Gm is the shear modulus of the matrix Km

and K the bulk moduli of the matrix and the sec-ond phase respectively and P the applied hydro-static pressure Dislocations are generated when[max reaches the nucleation stress for dislocationgeneration which can be theoretically predicted ordetermined experimen tally338

Another manner in which shear stresses are gener-ated in polycrystalline materials through the simpleapplication of hydrostatic pressure is through theanisotropy of elastic constants91128 Crystals of allsystems except the cubic system can change shapewhen subjected to hydrostatic pressure cubic crystalshave isotropic bulk moduli The volume compress-ibility which is the inverse of the bulk modulus isthe pressure induced change in volume of a crystalnormalised to its original volume and the linearcompressibility k is the amount of pressure inducedlength change in a straight line normalised to itsoriginal length For the cubic system k is independentof orientation and is related to the elastic compliance5ij through

k = 511 + S12 bull bull bullbull bull (3)For the trigonal hexagonal and tetragonal systemstwo constants are required the value in the a directionka and the value in the c direction kc These compress-ibilities are related to the elastic compliance 5ij by

Effects of superimposed pressure onstress state in cylindrical specimensConditions present before necking incylindrical specimensPlastic deformation in metallic systems tested at lowhomologous temperatures primarily occurs via dislo-cation generation andor movement via shear stressesoften referred to as conservative motion or glidePlastic deformation under such conditions occurswhen the effective stress (j equals the yield strengthin tension (Jy where the effective stress is given as

- 1 ( )2 ( )2 ( )2] 120=0[(J1-(J2 + 02-(J3 + (J3-(J1

(1)and (Jb (J2 and (J3 represent the principal stressesThe application of a purely hydrostatic stress (ie(J1 = 02 = (J3) produces no shear stress in a homo-geneous and isotropic material as shown by the 3-Dyield surface plotted in stress space in Fig 3 Ahydrostatic stress is represented as the axis of thecylinder in Fig 3 and since such stresses never touchthe yield surface there should be no effect ofpressurisationpressure soaking on the subsequentflow behaviour when uniaxial testing is conducted atatmospheric pressure Pressurisation in this casedenotes the simple application of hydrostatic pressureto a material and its subsequent removal Thereshould similarly be little effect of superimposed press-ure on yielding when testing is conducted on acylindrical specimen in the presence of a confining(ie hydrostatic) pressure as the stress state up to theultimate tensile stress (UTS) (ie before necking) insuch specimens consists of the uniaxial stress plusany superimposed hydrostatic pressure

However simple pressurisation can serve as ameans for generating dislocations in a materialaround inclusions and other defects as there are local

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 153

1

4 Yield surface plotted in principal stress spacefor material containing void fraction of a 0057and b 0180 (Ref 336)

1

1

a~l 05cr

o~ta

-05

-1

-1

(a)

(b)

The linear compressibility in any other direction kris given by

kr = ka + (ke - ka)r2 (6)

where r is the direction cosine with subject to thec axis

If non-cubic metals can change shape because ofpressurisation then a random aggregate of manycrystals when subjected to unit hydrostatic pressurewill develop shear stresses across grain boundaries Itis this shear stress which produces dislocation gener-ation in anisotropic materials

The degree of anisotropy in these non-cubic systemsis given in terms of the ratio keka The anisotropy ofa number of hexagonal metals is given in Table 3Those metals with a high degree of anisotropy Cdand Zn have been shown91339 to require only modestlevels of pressure ( 300 MPa) to induce plastic strainin the grains while metals with ratios close to one(where a cubic metal equals 10) Zr and Mg requiredthe highest pressures ( 2middot6 GPa) to produce onlytrace amounts of plastic deformation Although TEManalyses have confirmed the presence of pressureinduced dislocations around inclusions in less pureFe and Fe-C alloys containing inclusions65139 highpurity cubic metals such as Cu AI Fe and Ni haveshown no such plastic deformation after pressuris-ation to levels up to 1 GPa (Refs 109 339)

Porous materials consisting of either interconnectedor isolated pores are also highly pressure sensitive340provided the pressure medium is shielded from thespecimen to prevent ingress of the pressure medium(ie gas liquid) into the pores The 3-D yield loci forsuch materials are distinctly different from that shownin Fig 3 for homogeneous and isotropic materialsShown in Fig 4 are 3-D yield loci for porous materialscontaining increasing levels of porosity335336341342It is clear that the application of a hydrostatic pressureof sufficient magnitude in these cases can touch theyield surface and thereby produce plastic flowExamples of such effects are provided in works onporous Fe (Refs 62 137)

where Oflow is the flow stress a the minimum specimenradius R the radius of curvature at the neck or notchand rn the distance from the centre along the planeof the neck

Since the notchneck geometry will often changewith additional deformation the level of triaxialtensile stress resulting from deformation of such

International Materials Reviews 1998 Vol 43 NO4

mens) when subsequently tested in tension also experi-ence triaxial tensile stresses in the neckednotchedregion In this case the major difference between thenecked region which evolved during deformation andthat simulated by prenotching a pristine (ie non-deformed) specimen relates to the differences indeformation history (and any damage) present in thenecked region as compared to the notched regionBridgman provided an estimate of the additionalhydrostatic tension OT in the plane of a neck ornotch2436 as

Conditions present past necking incylindrical specimensOnce a neck begins to form in a cylindrical tensilespecimen tested at atmospheric pressure triaxialtensile stresses develop in the necked region Boththe magnitude and location of such triaxial stressesvary with location in the neck which develops withadditional deformation Prenecked (eg notched speci-

Table 3 Linear compressibility and anisotropyfactors for some non-cubic materials(Refs 128 339)

Lattice ratioLinear compressibility MPa

Metal cia c axis ke a axis ka Ratio keka

Cadmium 18856 1890 x 106 217 X 106 870Zinc 18564 1341 x 106 201 X 106 670Bismuth 26095 1645 x 106 684 X 106 240Magnesium 16235 1016 x 106 1016 X 106 1middot00Zirconium 1middot5931 380 x 106 3middot80 X 106 1middot00Titanium 15870 270 x 106 270 X 106 100Beryllium 15684 227 x 106 291 X 106 078

(a 12 )

OT = Oflow In 1 + 2R - 2a~ (7)

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154 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Superimposed Hydrostatic Pressure MPa

4340 tenlpered 3000C 152

4340 tempered (eQ 5000C 152

4340 tempered 7000C 152

o 4310-Lower Yield 133

bullbull 4330-Lower Yield 113

6 01 Tool Steel Hard 152

6 01 Tool Steel Mediunl 152

6 01 Tool Steel Soft 152

[S ri-V Steel 9500C FRT 152

fpound Ti-V Steel 700degC FRT 15~

bull 7075AI-T651(TR) 5051

bull 7075AI-T65 I(WR) 5051

T 7075AI-T65I (RW) 5051

() 201411 1(21)

EE BY -80 1ower Yield 134

bull Maraging-Unaged (Ten) 134

bull Maraging-Unaged (Comp) ]34

bull Maraging-Aged (Ten) 134

bull1200

(a)

bullbull

1000

EB

[SJ

800600400200

bull bull bull bullbullbullII bullbull JI bullbull Q bullbull bull

~ 6III II II bull

j 6 i i6

o

20

o

=~~ 15Q)~~

rJ)

0

~ 10~

e~ 05Z

~~ 1500

2000

=~eJ)

~ 1000~~

rJ)

e-Q)

~

00(b)

(gt 2124J() () I

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure

5 Effect of pressure on yield strength of various bee and fcc metallic alloys

specimens will vary past necking in the cylindricalspecimen Thus while the level of superimposedhydrostatic pressure has been kept relatively constantin many of the studies listed in Tables 1 and 2 thetriaxial stresses present in the neck during tests withsuperimposed pressure will depend on a variety offactors including the neck geometry level of superim-posed pressure and the flow stress of the materialIt is important to note that some studies investigat-ing the effects of superimposed pressure on tensiontests have been conducted under conditions suchthat compressive triaxial stresses were present in thenecked region In these cases the levels of superim-posed pressure were high enough to overcome thetriaxial tensile stresses which developed in the evolv-ing neck Thus the ability to monitor visually thedevelopment of the neck during tests with superim-posed pressure as described above or conductinginterrupted tests where the neck can be physicallymeasured outside of the high pressure environmenthas some merits858689103197213

Effects of superimposed pressure onflow behaviourEffects of superimposed pressure onyield stressFigures 5-8 summarise published data on the effectsof pressurisationpressure soaking as well as tensiletesting at different levels of superimposed hydrostaticpressure on the yield strength typically reported asthe 0middot2 offset yield strength In the former tests theyield strength was measured at atmospheric pressureafter pressurisation while the measurements of yieldstress in the latter cases occurred during tensile testsconducted with superimposed hydrostatic pressureThe pressure medium utilised in the studies summar-ised was either an oil medium or Ar gas and wasconfirmed to be hydrostatic Figure 5 summarisesdata obtained on a variety of steels and aluminiumalloys while Fig 6 shows similar data obtained on avariety of single phase metals possessing a bcc crystalstructure Figure 7 is a plot of the same type of

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 155

___bull __ Ar111co Iron 65

5b 6b 7b and 8b are plots of the ratio of the yieldstrength obtained at pressure (or after pressure soak-ing) to that of the control material (ie no pressuresoaking) in the manner utilised by a number ofinvestigators henceforth this is called the normalisedyield strength Pressure independent yielding is rep-resented by the horizontal line at 1middot0 for the normal-ised yield strength in Figs 5b-8b It is clear fromFig 5a that a number of conventional structuralmetallic alloys exhibit nominally pressure independ-ent yielding behaviour as predicted by equation (1)Slight positive deviations for monolithic materials (ienormalised yield strengthgt 1 in Fig 5b) have beenexplained as in part due to the pressure depend-ence of the shear modulus which though modestis non-zero for various metallic materials136Models313314 have been developed to predict suchpressure dependent yielding in metallic materials andmetallic glasses321-323 and a few studies have invokedsuch models to explain such pressure dependence ofthe yield stress136 It should be noted that there havebeen observations of materials which exhibit muchgreater positive deviations than those of the monolithicmetals summarised in Fig 5a and b For example ithas been clearly shown that superimposed pressuresignificantly inhibits dislocation mobility in LiFthereby elevating the flow stress above that obtainedat atmospheric pressure176

It is also clear that some of the monolithic metalsshown in Fig 5a and b as well as a variety of bccmetals (cf Fig 6a and b) and certain chemistries ofthe intermetallic NiAI shown in Fig7a and b ex-hibit a significant decrease in the yield strength afterpressure soaking or during tests conducted withsuperimposed pressure In these cases the materialstypically exhibited a yield point and Liiders exten-sion before pressure soaking or testing with superim-posed pressure Pressurisation (andor testing withpressure) was shown to remove the yield pointand Liiders strain and thereby reduce the yieldstrength155157159161162166167as illustrated for castextruded NiAI in Fig 7c As shown in Figs 6a andband 7a and b large reductions in yield strengthwere obtained in Fe (Refs 65 147) Cr (Refs 59 6466 72) and commercially pure NiAI (Refs 155 157161-163) that had been cast and extruded ExtensiveTEM analyses in these cases revealed that pressureinduced dislocation generation occurred at non-metallic inclusions and other inhomogeneities in thesematerials6465155157158161an example of which isshown in Fig 7d (Ref 157) The generation of thesemobile pressure induced dislocations thereby reducedthe yield strength while subsequent thermal agingstudies conducted for sufficient time-temperaturecombinations at atmospheric pressure enabled relock-ing of the dislocations by interstitial impurities (egC) and a return of the yield point and Liidersstrain6465107147166as illustrated for NiAI in Fig7c(Ref 159) Similar studies166167 conducted on highpurity NiAI failed to reveal a yield point and anysubsequent effect of pressurisation on the yield stressas shown in Fig 7a and b consistent with sucharguments Pressurisation of the largest grained Fein Fig 6a and b (Ref 147) to increasingly higherpressures eventually produced excessive generation

International Materials Reviews 1998 Vol 43 NO4

1200

(a)

(b)

---)

1000800600

~_-----1-~ - --

400200

- - Chromium 64

bull - Iodide Chromium 72

Superimposed Hydrostatic Pressure MPa

bull ~ ~- Y- -y_~~~ - - -9

-------

cOil 15cQJ

000 10~~5 050Z

000

800

eo 700~~ 600pound 500eiJcCJ 400V)

0 300~~ 200

100o

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

20

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

6 Effeet of pressure on yield strength of variousbee metals GS grain size

--0 Fc GS=11Jlnl 147

-0 Fe GS=14Jlm 147

-[S- Fe GS=19Jlm 147

-83- - Fe GS=30Jlm 147

-- - Fe GS=450~lIn 147

6 - - PM T 72- ungsten

-pound --Arc-Melted Tunsten 72

information for the intermetallic NiAI which possessesa B2 (ie bcc derivative) crystal structure while Fig 8is a plot of data from more recent work on compositesbased on either aluminium or magnesium alloymatrixes The data reported for the control materials(ie no pressure soaking) occur on the ordinate at0middot1 MPa (ie atmospheric pressure) Figures 5a 6a7a and 8a summarise the reported values for theyield strength obtained either during tension testswith superimposed pressure or after pressure soakingat the levels of hydrostatic pressure indicated Figures

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156 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullNill Cast and extruded 161

-[S)- - CP-NiAI Prepressurised 166

-EB - - - HP NAlP d 166- 1 repressunse

- -- - - - NiAI-NPrepressurised 166

50

300

(a)

1500

EB

(b)

middotmiddotlSI

__

middotEB

-bullbull-

bull

1000

-----------

1

500

_------------ --- -_---

Superimposed Hydrostatic Pressure MPa

100

50

20

00

o

c~ 15QJl-rj~ 10~8~ 05Z

oo 500 1000 1500

Superimposed Hydrostatic Pressure MPa

el~~ 200

250

o annealedp ~a~~a p ~a~~a p ~~~aT = 200degC 2h T = 400degC 2h

Strain

(c)d

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure c stress-strain curvesof polycrystalline NiAI tested in tension after annealing at 82JOC for 2 h pressurised to 14 GPa and tested at atmospheric pressure and afteraging pressurised specimens at either 200degC or 400degC for 2 h (Ref 159) (arrows show proportional limit) d dislocations being punched from Zrinclusion in NiAI pressurised to 1middot4 GPa (Refs 156 157 160 161)

7 Effect of pressure on yield strength of NiAI

of dislocations and a slight increase in the yieldstrength because of work hardening Little effect ofpressurisation was 0bserved on higher strengthPowder metallurgy produced NiAI (cf Fig7a

International Materials Reviews 1998 Vol 43 No4

and b)166 or W as well as arc-melted W (cf Fig6aand b) 72 in part due to the higher strengths of thematerials tested and the limited range of pressuresutilised

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 157

500

600(a)

Effects of pressure on work hardeningexponent nThe effects of testing with superimposed pressureon the work hardening exponent n have beeninfrequently studied Figure 9a and b illustrates theexperimentally measured effect of superimposed press-ure on n for a high strength aluminium alloy(7075- T651) tested in different orientations withrespect to the rolling direction Testing was conductedwith superimposed pressure on either uniaxial tensionspecimens or plane strain tension specimens andgenerally revealed an increase in n with increasingpressure The authors5051 indicated that such obser-vations could be related to the amount of secondphase particles which could punch out dislocationloops because of their smaller compressibility in amanner analogous to that described above for thecomposite materials

yield stress apparently arises because of pressureinduced dislocation generation around the reinforce-ment which increases significantly the local dislo-cation density thereby providing local hardening anda higher yield strength192195196 Transmission elec-tron microscope studies have confirmed that suchevents can occur provided the pressurisation is con-ducted at a large enough pressure to generate shearstresses of sufficient magnitude near the reinforce-ment192 Testing with superimposed pressure has alsobeen shown to inhibit the accumulation of damage(eg void initiation and growth) in such materials Asthe accumulation of damage reduces the load bearingarea and instantaneous modulus in such compositesand thereby reduces the strain hardening rate press-ure induced damage suppression has been proposedas also contributing to the elevated flow stressesobtained during tests conducted with superimposedpressure192196201 This point is further discussedbelow when summarising the effects of confiningpressure on the UTS In addition recent work hasalso shown that the level of residual stress in thematrix and reinforcement can be changed via pressur-isation343344 Finally various models315-320 have indi-cated that the presence of the non-deformingreinforcement particles provides constrained flow andenhances the flow stress of the matrix The super-position of pressure during tension testing shouldcounteract this effect as illustrated in a fewpapers318-320

15001000

== 0---

~ - - - ---= = = t0- -- - -

(b)

500Superimposed Hydrostatic Pressure MPa

oo

20

EZ 05-

- --6--- 2014AI-20SiCp 13 Jlm-AE 152201

-J - - 2014AI-20SiCp 13 Jlm-T6 152201

-1- - - 2124AI-14SiCw 1 Jlrn-UA 152201

-T---- 2124AI-14SiCw 1 ~m-OA 152201

-X - AI-AI Ni l~m 1523

0-- IIOOAJ-IOAI)O_~ 193

ltgt 193- -- 1100AI-15Al)0 -

- -0- - - 6061AI-15AJ 0 13lrn-UA 1952 3

-- -0- -- 6061AI-15AI 0 (13lm-OA 1952 3

- - -[SJ- - - 6061AI-15At) 0 13~ln-UA 185_ 3

- - -EB- - - 6090AI-25SiCp-SA 193

- - -- - - 6090AI-25SiCp-T6 193

-0- AZ91-19SiCp 15~lTn-T6 193

-e- AZ91-20SiCp52-lIn-T6 J93

c ~~~1-~ 200l x~ -X- X- y

100

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

8 Effect of pressure on yield strength ofdiscontinuously reinforced metal matrixcomposites

The largest changes in the yield strength obtainedeither after pressurisation or during tests with super-imposed pressure have been exhibited by compositematerials as shown in Fig 8a and b (Refs 152 185191-196 198 200 201) One source of the enhanced

Superimposed Hydrostatic Pressure MPa

00o 500 1000 1500 Effects of pressure on UTS

The experimental data for the UTS obtained viatension testing with a range of superimposed pressuresare provided for both monolithic metals as well ascomposites in Figs 10-15 As indicated above thestress state at the UTS (ie before necking) in suchspecimens consists of the uniaxial stress plus anysuperimposed hydrostatic pressure Data obtainedfrom some of Bridgmans original works are providedin Figs 10-13 for a variety of ferrous based systemsheat treated to different strength levels and micro-structures Figure 14a summarises similar data for avariety of other ferrous and non-ferrous structuralmaterials Figure 14b provides the ratio of the UTS

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158 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-6- _ TR uniaxialmiddotmiddotAmiddot TR plane strain-0 --- TW uniaxial

----e TW plane strain-0 - WRuniaxialbull - WRplanc strain

- --0 RW uniaxial- -+- - RW plane strain

-fSJ- Fe-034C-O75Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-045C-O83Mn-OO l6P-O035S-O19Si (as-received)

o normalised l650degF---0 annealed fine-grained- -6- annealed coarse-grained

- - - - - brine-quenchedtenlpered 600degF- - -+- - - brine-quenchedtempered 600degF-- -bull- - -- brine-quenchedtempered 900degF

015 3000

3000

middot11bull

1500 2000 25001000500Superimposed Hydrostatic Pressure MPa

o-- -0--

-6---e----+- -

--SJ-- Fe-O68C-O 7lMn-OO l3P-O025S-O19Si (as-received)

----0 --- Fe-O9C-O47Mn-O015P-O036S-OllSi (as-received)normalised 1650degFannealed fine-grainedannealed coarse-grainedbrine-quenchedspherodisedbrine-quenchedtempered 600degFbrine-quenchedtenlpered 900degF

bullbullbull

oo

2500

500

ce~E 1500rrJ~J 1000

10 Effect of pressure on UTS of various steelstested by Bridgman36

600

(a)

500 600

500

IImiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

middot0-middot -0

400

400

0

300

300

200

200

(b)

100

100Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

bullbull - A R bullbull

~ bull ~

000o

= 200Q)

=oc0lt

~ 150~=2

Q)C

100tt==~ 050eoZ 000

o

a n v hydrostatic pressure b normalised n v superimposedhydrostatic pressure

9 Effect of pressure on strain hardening exponentn of 7075AI- T651 (Refs 50 51)

3000

11 Effect of pressure on UTS of various steelstested by Bridgman36

Superimposed Hydrostatic Pressure MPa

500o

o -0

1500 2000 2500 30001000500

bullbull middot11II bull

~o Q ~omiddot omiddot

6 middot0middot omiddotmiddotmiddot=ltgt 6

1000

2500

ri1~ 1500J

~ 2000E

obtained at high pressure to that obtained at atmos-pheric pressure and a normalised UTS of 1middot0 indicatesno measurable effect of superimposed pressure onthe UTS The data for the monolithic metalsshown in Figs 10-13 as well as those summar-ised in Fig 14a and b indicate that superimposedpressure generally has a relatively minor effect on theUTS of most monolithic metals though someexceptions are shown Figure 15a and b illustratesthat composite materials often exhibit significantpressure dependent values for the UTS This hasbeen attributed152185189-201 to the pressure inducedsuppression of damage associated with the reinforce-ment and the matrix (eg void initiationgrowthcoalescence) which is covered in more detail in thefollowing sections on fracture behaviour

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 159

Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

A-+

bull -- -

0middot ------ -----()---6 - - - -

-8

iJII

-4-

-8-

---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

-8--- -lt)-

--

1000

5000

4000

C~ 3000~rJ5

2000 l-3~0

o S - - ~ lJS

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

I I I I I Iii I i

- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

3000

2500 -

d )000 f~~ -

~ 1500

~ middot_cmiddot- ~1000 ~_ibullbullbullbullbull~ - - -- - -- --0

s ti

500

12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure llPa

Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

- - -fr-

---]--

----T-

---0--

- - -lS -

------ - --(gt

--+-0-

4340 tempered 3000e 152

4340 tempered 5000e I 52

4340 tempered 7000e 152

01 Tool Steel Hard 152

01 Tool Steel Medium 152

01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

o 2124AI-14SiCw IJlm-UA 152201

bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

-+ Cu-28W 152

- - - -() - - - AI- Al Ni 152-

800

- - - -----------

~z~~~---~-----~bull-----~200

(a)

ts------6---1---------------- ------~

(b)

20

oo 100 WO ~O 400 ~O WO mo WO

Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

05

100

1000

1000

(a)

(b)

800

800600

600400

400

lZ91 19i

200

200Superimposed Hydrostatic Pressure MPa

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot-[H

----- ------0--middot- ----0

------6--- --6- ----------fJ--- --6

-----[S]----- ----[S]

-1-- - - - - - gtJ- - - - - - -Y- - -- - - -I- - - - - - gtJ

- -_~ ~~-~----- ~ _

middotmiddot~~-plusmn~middot~1middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

Superimposed Hydrostatic Pressure MPa

(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

~~ 1500

rJ5~ 1000

500

00

20

1500~~8 10l-o0Z

05

000

categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

International Materials Reviews 1998 Vol 43 No4

Page 9: Effects of Hydro Static Pressure on Mechanical

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 153

1

4 Yield surface plotted in principal stress spacefor material containing void fraction of a 0057and b 0180 (Ref 336)

1

1

a~l 05cr

o~ta

-05

-1

-1

(a)

(b)

The linear compressibility in any other direction kris given by

kr = ka + (ke - ka)r2 (6)

where r is the direction cosine with subject to thec axis

If non-cubic metals can change shape because ofpressurisation then a random aggregate of manycrystals when subjected to unit hydrostatic pressurewill develop shear stresses across grain boundaries Itis this shear stress which produces dislocation gener-ation in anisotropic materials

The degree of anisotropy in these non-cubic systemsis given in terms of the ratio keka The anisotropy ofa number of hexagonal metals is given in Table 3Those metals with a high degree of anisotropy Cdand Zn have been shown91339 to require only modestlevels of pressure ( 300 MPa) to induce plastic strainin the grains while metals with ratios close to one(where a cubic metal equals 10) Zr and Mg requiredthe highest pressures ( 2middot6 GPa) to produce onlytrace amounts of plastic deformation Although TEManalyses have confirmed the presence of pressureinduced dislocations around inclusions in less pureFe and Fe-C alloys containing inclusions65139 highpurity cubic metals such as Cu AI Fe and Ni haveshown no such plastic deformation after pressuris-ation to levels up to 1 GPa (Refs 109 339)

Porous materials consisting of either interconnectedor isolated pores are also highly pressure sensitive340provided the pressure medium is shielded from thespecimen to prevent ingress of the pressure medium(ie gas liquid) into the pores The 3-D yield loci forsuch materials are distinctly different from that shownin Fig 3 for homogeneous and isotropic materialsShown in Fig 4 are 3-D yield loci for porous materialscontaining increasing levels of porosity335336341342It is clear that the application of a hydrostatic pressureof sufficient magnitude in these cases can touch theyield surface and thereby produce plastic flowExamples of such effects are provided in works onporous Fe (Refs 62 137)

where Oflow is the flow stress a the minimum specimenradius R the radius of curvature at the neck or notchand rn the distance from the centre along the planeof the neck

Since the notchneck geometry will often changewith additional deformation the level of triaxialtensile stress resulting from deformation of such

International Materials Reviews 1998 Vol 43 NO4

mens) when subsequently tested in tension also experi-ence triaxial tensile stresses in the neckednotchedregion In this case the major difference between thenecked region which evolved during deformation andthat simulated by prenotching a pristine (ie non-deformed) specimen relates to the differences indeformation history (and any damage) present in thenecked region as compared to the notched regionBridgman provided an estimate of the additionalhydrostatic tension OT in the plane of a neck ornotch2436 as

Conditions present past necking incylindrical specimensOnce a neck begins to form in a cylindrical tensilespecimen tested at atmospheric pressure triaxialtensile stresses develop in the necked region Boththe magnitude and location of such triaxial stressesvary with location in the neck which develops withadditional deformation Prenecked (eg notched speci-

Table 3 Linear compressibility and anisotropyfactors for some non-cubic materials(Refs 128 339)

Lattice ratioLinear compressibility MPa

Metal cia c axis ke a axis ka Ratio keka

Cadmium 18856 1890 x 106 217 X 106 870Zinc 18564 1341 x 106 201 X 106 670Bismuth 26095 1645 x 106 684 X 106 240Magnesium 16235 1016 x 106 1016 X 106 1middot00Zirconium 1middot5931 380 x 106 3middot80 X 106 1middot00Titanium 15870 270 x 106 270 X 106 100Beryllium 15684 227 x 106 291 X 106 078

(a 12 )

OT = Oflow In 1 + 2R - 2a~ (7)

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154 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Superimposed Hydrostatic Pressure MPa

4340 tenlpered 3000C 152

4340 tempered (eQ 5000C 152

4340 tempered 7000C 152

o 4310-Lower Yield 133

bullbull 4330-Lower Yield 113

6 01 Tool Steel Hard 152

6 01 Tool Steel Mediunl 152

6 01 Tool Steel Soft 152

[S ri-V Steel 9500C FRT 152

fpound Ti-V Steel 700degC FRT 15~

bull 7075AI-T651(TR) 5051

bull 7075AI-T65 I(WR) 5051

T 7075AI-T65I (RW) 5051

() 201411 1(21)

EE BY -80 1ower Yield 134

bull Maraging-Unaged (Ten) 134

bull Maraging-Unaged (Comp) ]34

bull Maraging-Aged (Ten) 134

bull1200

(a)

bullbull

1000

EB

[SJ

800600400200

bull bull bull bullbullbullII bullbull JI bullbull Q bullbull bull

~ 6III II II bull

j 6 i i6

o

20

o

=~~ 15Q)~~

rJ)

0

~ 10~

e~ 05Z

~~ 1500

2000

=~eJ)

~ 1000~~

rJ)

e-Q)

~

00(b)

(gt 2124J() () I

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure

5 Effect of pressure on yield strength of various bee and fcc metallic alloys

specimens will vary past necking in the cylindricalspecimen Thus while the level of superimposedhydrostatic pressure has been kept relatively constantin many of the studies listed in Tables 1 and 2 thetriaxial stresses present in the neck during tests withsuperimposed pressure will depend on a variety offactors including the neck geometry level of superim-posed pressure and the flow stress of the materialIt is important to note that some studies investigat-ing the effects of superimposed pressure on tensiontests have been conducted under conditions suchthat compressive triaxial stresses were present in thenecked region In these cases the levels of superim-posed pressure were high enough to overcome thetriaxial tensile stresses which developed in the evolv-ing neck Thus the ability to monitor visually thedevelopment of the neck during tests with superim-posed pressure as described above or conductinginterrupted tests where the neck can be physicallymeasured outside of the high pressure environmenthas some merits858689103197213

Effects of superimposed pressure onflow behaviourEffects of superimposed pressure onyield stressFigures 5-8 summarise published data on the effectsof pressurisationpressure soaking as well as tensiletesting at different levels of superimposed hydrostaticpressure on the yield strength typically reported asthe 0middot2 offset yield strength In the former tests theyield strength was measured at atmospheric pressureafter pressurisation while the measurements of yieldstress in the latter cases occurred during tensile testsconducted with superimposed hydrostatic pressureThe pressure medium utilised in the studies summar-ised was either an oil medium or Ar gas and wasconfirmed to be hydrostatic Figure 5 summarisesdata obtained on a variety of steels and aluminiumalloys while Fig 6 shows similar data obtained on avariety of single phase metals possessing a bcc crystalstructure Figure 7 is a plot of the same type of

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 155

___bull __ Ar111co Iron 65

5b 6b 7b and 8b are plots of the ratio of the yieldstrength obtained at pressure (or after pressure soak-ing) to that of the control material (ie no pressuresoaking) in the manner utilised by a number ofinvestigators henceforth this is called the normalisedyield strength Pressure independent yielding is rep-resented by the horizontal line at 1middot0 for the normal-ised yield strength in Figs 5b-8b It is clear fromFig 5a that a number of conventional structuralmetallic alloys exhibit nominally pressure independ-ent yielding behaviour as predicted by equation (1)Slight positive deviations for monolithic materials (ienormalised yield strengthgt 1 in Fig 5b) have beenexplained as in part due to the pressure depend-ence of the shear modulus which though modestis non-zero for various metallic materials136Models313314 have been developed to predict suchpressure dependent yielding in metallic materials andmetallic glasses321-323 and a few studies have invokedsuch models to explain such pressure dependence ofthe yield stress136 It should be noted that there havebeen observations of materials which exhibit muchgreater positive deviations than those of the monolithicmetals summarised in Fig 5a and b For example ithas been clearly shown that superimposed pressuresignificantly inhibits dislocation mobility in LiFthereby elevating the flow stress above that obtainedat atmospheric pressure176

It is also clear that some of the monolithic metalsshown in Fig 5a and b as well as a variety of bccmetals (cf Fig 6a and b) and certain chemistries ofthe intermetallic NiAI shown in Fig7a and b ex-hibit a significant decrease in the yield strength afterpressure soaking or during tests conducted withsuperimposed pressure In these cases the materialstypically exhibited a yield point and Liiders exten-sion before pressure soaking or testing with superim-posed pressure Pressurisation (andor testing withpressure) was shown to remove the yield pointand Liiders strain and thereby reduce the yieldstrength155157159161162166167as illustrated for castextruded NiAI in Fig 7c As shown in Figs 6a andband 7a and b large reductions in yield strengthwere obtained in Fe (Refs 65 147) Cr (Refs 59 6466 72) and commercially pure NiAI (Refs 155 157161-163) that had been cast and extruded ExtensiveTEM analyses in these cases revealed that pressureinduced dislocation generation occurred at non-metallic inclusions and other inhomogeneities in thesematerials6465155157158161an example of which isshown in Fig 7d (Ref 157) The generation of thesemobile pressure induced dislocations thereby reducedthe yield strength while subsequent thermal agingstudies conducted for sufficient time-temperaturecombinations at atmospheric pressure enabled relock-ing of the dislocations by interstitial impurities (egC) and a return of the yield point and Liidersstrain6465107147166as illustrated for NiAI in Fig7c(Ref 159) Similar studies166167 conducted on highpurity NiAI failed to reveal a yield point and anysubsequent effect of pressurisation on the yield stressas shown in Fig 7a and b consistent with sucharguments Pressurisation of the largest grained Fein Fig 6a and b (Ref 147) to increasingly higherpressures eventually produced excessive generation

International Materials Reviews 1998 Vol 43 NO4

1200

(a)

(b)

---)

1000800600

~_-----1-~ - --

400200

- - Chromium 64

bull - Iodide Chromium 72

Superimposed Hydrostatic Pressure MPa

bull ~ ~- Y- -y_~~~ - - -9

-------

cOil 15cQJ

000 10~~5 050Z

000

800

eo 700~~ 600pound 500eiJcCJ 400V)

0 300~~ 200

100o

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

20

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

6 Effeet of pressure on yield strength of variousbee metals GS grain size

--0 Fc GS=11Jlnl 147

-0 Fe GS=14Jlm 147

-[S- Fe GS=19Jlm 147

-83- - Fe GS=30Jlm 147

-- - Fe GS=450~lIn 147

6 - - PM T 72- ungsten

-pound --Arc-Melted Tunsten 72

information for the intermetallic NiAI which possessesa B2 (ie bcc derivative) crystal structure while Fig 8is a plot of data from more recent work on compositesbased on either aluminium or magnesium alloymatrixes The data reported for the control materials(ie no pressure soaking) occur on the ordinate at0middot1 MPa (ie atmospheric pressure) Figures 5a 6a7a and 8a summarise the reported values for theyield strength obtained either during tension testswith superimposed pressure or after pressure soakingat the levels of hydrostatic pressure indicated Figures

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156 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullNill Cast and extruded 161

-[S)- - CP-NiAI Prepressurised 166

-EB - - - HP NAlP d 166- 1 repressunse

- -- - - - NiAI-NPrepressurised 166

50

300

(a)

1500

EB

(b)

middotmiddotlSI

__

middotEB

-bullbull-

bull

1000

-----------

1

500

_------------ --- -_---

Superimposed Hydrostatic Pressure MPa

100

50

20

00

o

c~ 15QJl-rj~ 10~8~ 05Z

oo 500 1000 1500

Superimposed Hydrostatic Pressure MPa

el~~ 200

250

o annealedp ~a~~a p ~a~~a p ~~~aT = 200degC 2h T = 400degC 2h

Strain

(c)d

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure c stress-strain curvesof polycrystalline NiAI tested in tension after annealing at 82JOC for 2 h pressurised to 14 GPa and tested at atmospheric pressure and afteraging pressurised specimens at either 200degC or 400degC for 2 h (Ref 159) (arrows show proportional limit) d dislocations being punched from Zrinclusion in NiAI pressurised to 1middot4 GPa (Refs 156 157 160 161)

7 Effect of pressure on yield strength of NiAI

of dislocations and a slight increase in the yieldstrength because of work hardening Little effect ofpressurisation was 0bserved on higher strengthPowder metallurgy produced NiAI (cf Fig7a

International Materials Reviews 1998 Vol 43 No4

and b)166 or W as well as arc-melted W (cf Fig6aand b) 72 in part due to the higher strengths of thematerials tested and the limited range of pressuresutilised

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 157

500

600(a)

Effects of pressure on work hardeningexponent nThe effects of testing with superimposed pressureon the work hardening exponent n have beeninfrequently studied Figure 9a and b illustrates theexperimentally measured effect of superimposed press-ure on n for a high strength aluminium alloy(7075- T651) tested in different orientations withrespect to the rolling direction Testing was conductedwith superimposed pressure on either uniaxial tensionspecimens or plane strain tension specimens andgenerally revealed an increase in n with increasingpressure The authors5051 indicated that such obser-vations could be related to the amount of secondphase particles which could punch out dislocationloops because of their smaller compressibility in amanner analogous to that described above for thecomposite materials

yield stress apparently arises because of pressureinduced dislocation generation around the reinforce-ment which increases significantly the local dislo-cation density thereby providing local hardening anda higher yield strength192195196 Transmission elec-tron microscope studies have confirmed that suchevents can occur provided the pressurisation is con-ducted at a large enough pressure to generate shearstresses of sufficient magnitude near the reinforce-ment192 Testing with superimposed pressure has alsobeen shown to inhibit the accumulation of damage(eg void initiation and growth) in such materials Asthe accumulation of damage reduces the load bearingarea and instantaneous modulus in such compositesand thereby reduces the strain hardening rate press-ure induced damage suppression has been proposedas also contributing to the elevated flow stressesobtained during tests conducted with superimposedpressure192196201 This point is further discussedbelow when summarising the effects of confiningpressure on the UTS In addition recent work hasalso shown that the level of residual stress in thematrix and reinforcement can be changed via pressur-isation343344 Finally various models315-320 have indi-cated that the presence of the non-deformingreinforcement particles provides constrained flow andenhances the flow stress of the matrix The super-position of pressure during tension testing shouldcounteract this effect as illustrated in a fewpapers318-320

15001000

== 0---

~ - - - ---= = = t0- -- - -

(b)

500Superimposed Hydrostatic Pressure MPa

oo

20

EZ 05-

- --6--- 2014AI-20SiCp 13 Jlm-AE 152201

-J - - 2014AI-20SiCp 13 Jlm-T6 152201

-1- - - 2124AI-14SiCw 1 Jlrn-UA 152201

-T---- 2124AI-14SiCw 1 ~m-OA 152201

-X - AI-AI Ni l~m 1523

0-- IIOOAJ-IOAI)O_~ 193

ltgt 193- -- 1100AI-15Al)0 -

- -0- - - 6061AI-15AJ 0 13lrn-UA 1952 3

-- -0- -- 6061AI-15AI 0 (13lm-OA 1952 3

- - -[SJ- - - 6061AI-15At) 0 13~ln-UA 185_ 3

- - -EB- - - 6090AI-25SiCp-SA 193

- - -- - - 6090AI-25SiCp-T6 193

-0- AZ91-19SiCp 15~lTn-T6 193

-e- AZ91-20SiCp52-lIn-T6 J93

c ~~~1-~ 200l x~ -X- X- y

100

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

8 Effect of pressure on yield strength ofdiscontinuously reinforced metal matrixcomposites

The largest changes in the yield strength obtainedeither after pressurisation or during tests with super-imposed pressure have been exhibited by compositematerials as shown in Fig 8a and b (Refs 152 185191-196 198 200 201) One source of the enhanced

Superimposed Hydrostatic Pressure MPa

00o 500 1000 1500 Effects of pressure on UTS

The experimental data for the UTS obtained viatension testing with a range of superimposed pressuresare provided for both monolithic metals as well ascomposites in Figs 10-15 As indicated above thestress state at the UTS (ie before necking) in suchspecimens consists of the uniaxial stress plus anysuperimposed hydrostatic pressure Data obtainedfrom some of Bridgmans original works are providedin Figs 10-13 for a variety of ferrous based systemsheat treated to different strength levels and micro-structures Figure 14a summarises similar data for avariety of other ferrous and non-ferrous structuralmaterials Figure 14b provides the ratio of the UTS

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158 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-6- _ TR uniaxialmiddotmiddotAmiddot TR plane strain-0 --- TW uniaxial

----e TW plane strain-0 - WRuniaxialbull - WRplanc strain

- --0 RW uniaxial- -+- - RW plane strain

-fSJ- Fe-034C-O75Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-045C-O83Mn-OO l6P-O035S-O19Si (as-received)

o normalised l650degF---0 annealed fine-grained- -6- annealed coarse-grained

- - - - - brine-quenchedtenlpered 600degF- - -+- - - brine-quenchedtempered 600degF-- -bull- - -- brine-quenchedtempered 900degF

015 3000

3000

middot11bull

1500 2000 25001000500Superimposed Hydrostatic Pressure MPa

o-- -0--

-6---e----+- -

--SJ-- Fe-O68C-O 7lMn-OO l3P-O025S-O19Si (as-received)

----0 --- Fe-O9C-O47Mn-O015P-O036S-OllSi (as-received)normalised 1650degFannealed fine-grainedannealed coarse-grainedbrine-quenchedspherodisedbrine-quenchedtempered 600degFbrine-quenchedtenlpered 900degF

bullbullbull

oo

2500

500

ce~E 1500rrJ~J 1000

10 Effect of pressure on UTS of various steelstested by Bridgman36

600

(a)

500 600

500

IImiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

middot0-middot -0

400

400

0

300

300

200

200

(b)

100

100Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

bullbull - A R bullbull

~ bull ~

000o

= 200Q)

=oc0lt

~ 150~=2

Q)C

100tt==~ 050eoZ 000

o

a n v hydrostatic pressure b normalised n v superimposedhydrostatic pressure

9 Effect of pressure on strain hardening exponentn of 7075AI- T651 (Refs 50 51)

3000

11 Effect of pressure on UTS of various steelstested by Bridgman36

Superimposed Hydrostatic Pressure MPa

500o

o -0

1500 2000 2500 30001000500

bullbull middot11II bull

~o Q ~omiddot omiddot

6 middot0middot omiddotmiddotmiddot=ltgt 6

1000

2500

ri1~ 1500J

~ 2000E

obtained at high pressure to that obtained at atmos-pheric pressure and a normalised UTS of 1middot0 indicatesno measurable effect of superimposed pressure onthe UTS The data for the monolithic metalsshown in Figs 10-13 as well as those summar-ised in Fig 14a and b indicate that superimposedpressure generally has a relatively minor effect on theUTS of most monolithic metals though someexceptions are shown Figure 15a and b illustratesthat composite materials often exhibit significantpressure dependent values for the UTS This hasbeen attributed152185189-201 to the pressure inducedsuppression of damage associated with the reinforce-ment and the matrix (eg void initiationgrowthcoalescence) which is covered in more detail in thefollowing sections on fracture behaviour

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 159

Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

A-+

bull -- -

0middot ------ -----()---6 - - - -

-8

iJII

-4-

-8-

---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

-8--- -lt)-

--

1000

5000

4000

C~ 3000~rJ5

2000 l-3~0

o S - - ~ lJS

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

I I I I I Iii I i

- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

3000

2500 -

d )000 f~~ -

~ 1500

~ middot_cmiddot- ~1000 ~_ibullbullbullbullbull~ - - -- - -- --0

s ti

500

12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure llPa

Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

- - -fr-

---]--

----T-

---0--

- - -lS -

------ - --(gt

--+-0-

4340 tempered 3000e 152

4340 tempered 5000e I 52

4340 tempered 7000e 152

01 Tool Steel Hard 152

01 Tool Steel Medium 152

01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

o 2124AI-14SiCw IJlm-UA 152201

bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

-+ Cu-28W 152

- - - -() - - - AI- Al Ni 152-

800

- - - -----------

~z~~~---~-----~bull-----~200

(a)

ts------6---1---------------- ------~

(b)

20

oo 100 WO ~O 400 ~O WO mo WO

Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

05

100

1000

1000

(a)

(b)

800

800600

600400

400

lZ91 19i

200

200Superimposed Hydrostatic Pressure MPa

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot-[H

----- ------0--middot- ----0

------6--- --6- ----------fJ--- --6

-----[S]----- ----[S]

-1-- - - - - - gtJ- - - - - - -Y- - -- - - -I- - - - - - gtJ

- -_~ ~~-~----- ~ _

middotmiddot~~-plusmn~middot~1middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

Superimposed Hydrostatic Pressure MPa

(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

~~ 1500

rJ5~ 1000

500

00

20

1500~~8 10l-o0Z

05

000

categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

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154 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Superimposed Hydrostatic Pressure MPa

4340 tenlpered 3000C 152

4340 tempered (eQ 5000C 152

4340 tempered 7000C 152

o 4310-Lower Yield 133

bullbull 4330-Lower Yield 113

6 01 Tool Steel Hard 152

6 01 Tool Steel Mediunl 152

6 01 Tool Steel Soft 152

[S ri-V Steel 9500C FRT 152

fpound Ti-V Steel 700degC FRT 15~

bull 7075AI-T651(TR) 5051

bull 7075AI-T65 I(WR) 5051

T 7075AI-T65I (RW) 5051

() 201411 1(21)

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bull Maraging-Unaged (Ten) 134

bull Maraging-Unaged (Comp) ]34

bull Maraging-Aged (Ten) 134

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o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure

5 Effect of pressure on yield strength of various bee and fcc metallic alloys

specimens will vary past necking in the cylindricalspecimen Thus while the level of superimposedhydrostatic pressure has been kept relatively constantin many of the studies listed in Tables 1 and 2 thetriaxial stresses present in the neck during tests withsuperimposed pressure will depend on a variety offactors including the neck geometry level of superim-posed pressure and the flow stress of the materialIt is important to note that some studies investigat-ing the effects of superimposed pressure on tensiontests have been conducted under conditions suchthat compressive triaxial stresses were present in thenecked region In these cases the levels of superim-posed pressure were high enough to overcome thetriaxial tensile stresses which developed in the evolv-ing neck Thus the ability to monitor visually thedevelopment of the neck during tests with superim-posed pressure as described above or conductinginterrupted tests where the neck can be physicallymeasured outside of the high pressure environmenthas some merits858689103197213

Effects of superimposed pressure onflow behaviourEffects of superimposed pressure onyield stressFigures 5-8 summarise published data on the effectsof pressurisationpressure soaking as well as tensiletesting at different levels of superimposed hydrostaticpressure on the yield strength typically reported asthe 0middot2 offset yield strength In the former tests theyield strength was measured at atmospheric pressureafter pressurisation while the measurements of yieldstress in the latter cases occurred during tensile testsconducted with superimposed hydrostatic pressureThe pressure medium utilised in the studies summar-ised was either an oil medium or Ar gas and wasconfirmed to be hydrostatic Figure 5 summarisesdata obtained on a variety of steels and aluminiumalloys while Fig 6 shows similar data obtained on avariety of single phase metals possessing a bcc crystalstructure Figure 7 is a plot of the same type of

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 155

___bull __ Ar111co Iron 65

5b 6b 7b and 8b are plots of the ratio of the yieldstrength obtained at pressure (or after pressure soak-ing) to that of the control material (ie no pressuresoaking) in the manner utilised by a number ofinvestigators henceforth this is called the normalisedyield strength Pressure independent yielding is rep-resented by the horizontal line at 1middot0 for the normal-ised yield strength in Figs 5b-8b It is clear fromFig 5a that a number of conventional structuralmetallic alloys exhibit nominally pressure independ-ent yielding behaviour as predicted by equation (1)Slight positive deviations for monolithic materials (ienormalised yield strengthgt 1 in Fig 5b) have beenexplained as in part due to the pressure depend-ence of the shear modulus which though modestis non-zero for various metallic materials136Models313314 have been developed to predict suchpressure dependent yielding in metallic materials andmetallic glasses321-323 and a few studies have invokedsuch models to explain such pressure dependence ofthe yield stress136 It should be noted that there havebeen observations of materials which exhibit muchgreater positive deviations than those of the monolithicmetals summarised in Fig 5a and b For example ithas been clearly shown that superimposed pressuresignificantly inhibits dislocation mobility in LiFthereby elevating the flow stress above that obtainedat atmospheric pressure176

It is also clear that some of the monolithic metalsshown in Fig 5a and b as well as a variety of bccmetals (cf Fig 6a and b) and certain chemistries ofthe intermetallic NiAI shown in Fig7a and b ex-hibit a significant decrease in the yield strength afterpressure soaking or during tests conducted withsuperimposed pressure In these cases the materialstypically exhibited a yield point and Liiders exten-sion before pressure soaking or testing with superim-posed pressure Pressurisation (andor testing withpressure) was shown to remove the yield pointand Liiders strain and thereby reduce the yieldstrength155157159161162166167as illustrated for castextruded NiAI in Fig 7c As shown in Figs 6a andband 7a and b large reductions in yield strengthwere obtained in Fe (Refs 65 147) Cr (Refs 59 6466 72) and commercially pure NiAI (Refs 155 157161-163) that had been cast and extruded ExtensiveTEM analyses in these cases revealed that pressureinduced dislocation generation occurred at non-metallic inclusions and other inhomogeneities in thesematerials6465155157158161an example of which isshown in Fig 7d (Ref 157) The generation of thesemobile pressure induced dislocations thereby reducedthe yield strength while subsequent thermal agingstudies conducted for sufficient time-temperaturecombinations at atmospheric pressure enabled relock-ing of the dislocations by interstitial impurities (egC) and a return of the yield point and Liidersstrain6465107147166as illustrated for NiAI in Fig7c(Ref 159) Similar studies166167 conducted on highpurity NiAI failed to reveal a yield point and anysubsequent effect of pressurisation on the yield stressas shown in Fig 7a and b consistent with sucharguments Pressurisation of the largest grained Fein Fig 6a and b (Ref 147) to increasingly higherpressures eventually produced excessive generation

International Materials Reviews 1998 Vol 43 NO4

1200

(a)

(b)

---)

1000800600

~_-----1-~ - --

400200

- - Chromium 64

bull - Iodide Chromium 72

Superimposed Hydrostatic Pressure MPa

bull ~ ~- Y- -y_~~~ - - -9

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000

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20

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

6 Effeet of pressure on yield strength of variousbee metals GS grain size

--0 Fc GS=11Jlnl 147

-0 Fe GS=14Jlm 147

-[S- Fe GS=19Jlm 147

-83- - Fe GS=30Jlm 147

-- - Fe GS=450~lIn 147

6 - - PM T 72- ungsten

-pound --Arc-Melted Tunsten 72

information for the intermetallic NiAI which possessesa B2 (ie bcc derivative) crystal structure while Fig 8is a plot of data from more recent work on compositesbased on either aluminium or magnesium alloymatrixes The data reported for the control materials(ie no pressure soaking) occur on the ordinate at0middot1 MPa (ie atmospheric pressure) Figures 5a 6a7a and 8a summarise the reported values for theyield strength obtained either during tension testswith superimposed pressure or after pressure soakingat the levels of hydrostatic pressure indicated Figures

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156 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullNill Cast and extruded 161

-[S)- - CP-NiAI Prepressurised 166

-EB - - - HP NAlP d 166- 1 repressunse

- -- - - - NiAI-NPrepressurised 166

50

300

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a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure c stress-strain curvesof polycrystalline NiAI tested in tension after annealing at 82JOC for 2 h pressurised to 14 GPa and tested at atmospheric pressure and afteraging pressurised specimens at either 200degC or 400degC for 2 h (Ref 159) (arrows show proportional limit) d dislocations being punched from Zrinclusion in NiAI pressurised to 1middot4 GPa (Refs 156 157 160 161)

7 Effect of pressure on yield strength of NiAI

of dislocations and a slight increase in the yieldstrength because of work hardening Little effect ofpressurisation was 0bserved on higher strengthPowder metallurgy produced NiAI (cf Fig7a

International Materials Reviews 1998 Vol 43 No4

and b)166 or W as well as arc-melted W (cf Fig6aand b) 72 in part due to the higher strengths of thematerials tested and the limited range of pressuresutilised

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 157

500

600(a)

Effects of pressure on work hardeningexponent nThe effects of testing with superimposed pressureon the work hardening exponent n have beeninfrequently studied Figure 9a and b illustrates theexperimentally measured effect of superimposed press-ure on n for a high strength aluminium alloy(7075- T651) tested in different orientations withrespect to the rolling direction Testing was conductedwith superimposed pressure on either uniaxial tensionspecimens or plane strain tension specimens andgenerally revealed an increase in n with increasingpressure The authors5051 indicated that such obser-vations could be related to the amount of secondphase particles which could punch out dislocationloops because of their smaller compressibility in amanner analogous to that described above for thecomposite materials

yield stress apparently arises because of pressureinduced dislocation generation around the reinforce-ment which increases significantly the local dislo-cation density thereby providing local hardening anda higher yield strength192195196 Transmission elec-tron microscope studies have confirmed that suchevents can occur provided the pressurisation is con-ducted at a large enough pressure to generate shearstresses of sufficient magnitude near the reinforce-ment192 Testing with superimposed pressure has alsobeen shown to inhibit the accumulation of damage(eg void initiation and growth) in such materials Asthe accumulation of damage reduces the load bearingarea and instantaneous modulus in such compositesand thereby reduces the strain hardening rate press-ure induced damage suppression has been proposedas also contributing to the elevated flow stressesobtained during tests conducted with superimposedpressure192196201 This point is further discussedbelow when summarising the effects of confiningpressure on the UTS In addition recent work hasalso shown that the level of residual stress in thematrix and reinforcement can be changed via pressur-isation343344 Finally various models315-320 have indi-cated that the presence of the non-deformingreinforcement particles provides constrained flow andenhances the flow stress of the matrix The super-position of pressure during tension testing shouldcounteract this effect as illustrated in a fewpapers318-320

15001000

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- --6--- 2014AI-20SiCp 13 Jlm-AE 152201

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ltgt 193- -- 1100AI-15Al)0 -

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-- -0- -- 6061AI-15AI 0 (13lm-OA 1952 3

- - -[SJ- - - 6061AI-15At) 0 13~ln-UA 185_ 3

- - -EB- - - 6090AI-25SiCp-SA 193

- - -- - - 6090AI-25SiCp-T6 193

-0- AZ91-19SiCp 15~lTn-T6 193

-e- AZ91-20SiCp52-lIn-T6 J93

c ~~~1-~ 200l x~ -X- X- y

100

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

8 Effect of pressure on yield strength ofdiscontinuously reinforced metal matrixcomposites

The largest changes in the yield strength obtainedeither after pressurisation or during tests with super-imposed pressure have been exhibited by compositematerials as shown in Fig 8a and b (Refs 152 185191-196 198 200 201) One source of the enhanced

Superimposed Hydrostatic Pressure MPa

00o 500 1000 1500 Effects of pressure on UTS

The experimental data for the UTS obtained viatension testing with a range of superimposed pressuresare provided for both monolithic metals as well ascomposites in Figs 10-15 As indicated above thestress state at the UTS (ie before necking) in suchspecimens consists of the uniaxial stress plus anysuperimposed hydrostatic pressure Data obtainedfrom some of Bridgmans original works are providedin Figs 10-13 for a variety of ferrous based systemsheat treated to different strength levels and micro-structures Figure 14a summarises similar data for avariety of other ferrous and non-ferrous structuralmaterials Figure 14b provides the ratio of the UTS

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158 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-6- _ TR uniaxialmiddotmiddotAmiddot TR plane strain-0 --- TW uniaxial

----e TW plane strain-0 - WRuniaxialbull - WRplanc strain

- --0 RW uniaxial- -+- - RW plane strain

-fSJ- Fe-034C-O75Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-045C-O83Mn-OO l6P-O035S-O19Si (as-received)

o normalised l650degF---0 annealed fine-grained- -6- annealed coarse-grained

- - - - - brine-quenchedtenlpered 600degF- - -+- - - brine-quenchedtempered 600degF-- -bull- - -- brine-quenchedtempered 900degF

015 3000

3000

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1500 2000 25001000500Superimposed Hydrostatic Pressure MPa

o-- -0--

-6---e----+- -

--SJ-- Fe-O68C-O 7lMn-OO l3P-O025S-O19Si (as-received)

----0 --- Fe-O9C-O47Mn-O015P-O036S-OllSi (as-received)normalised 1650degFannealed fine-grainedannealed coarse-grainedbrine-quenchedspherodisedbrine-quenchedtempered 600degFbrine-quenchedtenlpered 900degF

bullbullbull

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500

ce~E 1500rrJ~J 1000

10 Effect of pressure on UTS of various steelstested by Bridgman36

600

(a)

500 600

500

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middot0-middot -0

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bullbull - A R bullbull

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9 Effect of pressure on strain hardening exponentn of 7075AI- T651 (Refs 50 51)

3000

11 Effect of pressure on UTS of various steelstested by Bridgman36

Superimposed Hydrostatic Pressure MPa

500o

o -0

1500 2000 2500 30001000500

bullbull middot11II bull

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6 middot0middot omiddotmiddotmiddot=ltgt 6

1000

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obtained at high pressure to that obtained at atmos-pheric pressure and a normalised UTS of 1middot0 indicatesno measurable effect of superimposed pressure onthe UTS The data for the monolithic metalsshown in Figs 10-13 as well as those summar-ised in Fig 14a and b indicate that superimposedpressure generally has a relatively minor effect on theUTS of most monolithic metals though someexceptions are shown Figure 15a and b illustratesthat composite materials often exhibit significantpressure dependent values for the UTS This hasbeen attributed152185189-201 to the pressure inducedsuppression of damage associated with the reinforce-ment and the matrix (eg void initiationgrowthcoalescence) which is covered in more detail in thefollowing sections on fracture behaviour

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 159

Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

A-+

bull -- -

0middot ------ -----()---6 - - - -

-8

iJII

-4-

-8-

---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

-8--- -lt)-

--

1000

5000

4000

C~ 3000~rJ5

2000 l-3~0

o S - - ~ lJS

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

I I I I I Iii I i

- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

3000

2500 -

d )000 f~~ -

~ 1500

~ middot_cmiddot- ~1000 ~_ibullbullbullbullbull~ - - -- - -- --0

s ti

500

12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure llPa

Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

- - -fr-

---]--

----T-

---0--

- - -lS -

------ - --(gt

--+-0-

4340 tempered 3000e 152

4340 tempered 5000e I 52

4340 tempered 7000e 152

01 Tool Steel Hard 152

01 Tool Steel Medium 152

01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

o 2124AI-14SiCw IJlm-UA 152201

bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

-+ Cu-28W 152

- - - -() - - - AI- Al Ni 152-

800

- - - -----------

~z~~~---~-----~bull-----~200

(a)

ts------6---1---------------- ------~

(b)

20

oo 100 WO ~O 400 ~O WO mo WO

Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

05

100

1000

1000

(a)

(b)

800

800600

600400

400

lZ91 19i

200

200Superimposed Hydrostatic Pressure MPa

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot-[H

----- ------0--middot- ----0

------6--- --6- ----------fJ--- --6

-----[S]----- ----[S]

-1-- - - - - - gtJ- - - - - - -Y- - -- - - -I- - - - - - gtJ

- -_~ ~~-~----- ~ _

middotmiddot~~-plusmn~middot~1middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

Superimposed Hydrostatic Pressure MPa

(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

~~ 1500

rJ5~ 1000

500

00

20

1500~~8 10l-o0Z

05

000

categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 155

___bull __ Ar111co Iron 65

5b 6b 7b and 8b are plots of the ratio of the yieldstrength obtained at pressure (or after pressure soak-ing) to that of the control material (ie no pressuresoaking) in the manner utilised by a number ofinvestigators henceforth this is called the normalisedyield strength Pressure independent yielding is rep-resented by the horizontal line at 1middot0 for the normal-ised yield strength in Figs 5b-8b It is clear fromFig 5a that a number of conventional structuralmetallic alloys exhibit nominally pressure independ-ent yielding behaviour as predicted by equation (1)Slight positive deviations for monolithic materials (ienormalised yield strengthgt 1 in Fig 5b) have beenexplained as in part due to the pressure depend-ence of the shear modulus which though modestis non-zero for various metallic materials136Models313314 have been developed to predict suchpressure dependent yielding in metallic materials andmetallic glasses321-323 and a few studies have invokedsuch models to explain such pressure dependence ofthe yield stress136 It should be noted that there havebeen observations of materials which exhibit muchgreater positive deviations than those of the monolithicmetals summarised in Fig 5a and b For example ithas been clearly shown that superimposed pressuresignificantly inhibits dislocation mobility in LiFthereby elevating the flow stress above that obtainedat atmospheric pressure176

It is also clear that some of the monolithic metalsshown in Fig 5a and b as well as a variety of bccmetals (cf Fig 6a and b) and certain chemistries ofthe intermetallic NiAI shown in Fig7a and b ex-hibit a significant decrease in the yield strength afterpressure soaking or during tests conducted withsuperimposed pressure In these cases the materialstypically exhibited a yield point and Liiders exten-sion before pressure soaking or testing with superim-posed pressure Pressurisation (andor testing withpressure) was shown to remove the yield pointand Liiders strain and thereby reduce the yieldstrength155157159161162166167as illustrated for castextruded NiAI in Fig 7c As shown in Figs 6a andband 7a and b large reductions in yield strengthwere obtained in Fe (Refs 65 147) Cr (Refs 59 6466 72) and commercially pure NiAI (Refs 155 157161-163) that had been cast and extruded ExtensiveTEM analyses in these cases revealed that pressureinduced dislocation generation occurred at non-metallic inclusions and other inhomogeneities in thesematerials6465155157158161an example of which isshown in Fig 7d (Ref 157) The generation of thesemobile pressure induced dislocations thereby reducedthe yield strength while subsequent thermal agingstudies conducted for sufficient time-temperaturecombinations at atmospheric pressure enabled relock-ing of the dislocations by interstitial impurities (egC) and a return of the yield point and Liidersstrain6465107147166as illustrated for NiAI in Fig7c(Ref 159) Similar studies166167 conducted on highpurity NiAI failed to reveal a yield point and anysubsequent effect of pressurisation on the yield stressas shown in Fig 7a and b consistent with sucharguments Pressurisation of the largest grained Fein Fig 6a and b (Ref 147) to increasingly higherpressures eventually produced excessive generation

International Materials Reviews 1998 Vol 43 NO4

1200

(a)

(b)

---)

1000800600

~_-----1-~ - --

400200

- - Chromium 64

bull - Iodide Chromium 72

Superimposed Hydrostatic Pressure MPa

bull ~ ~- Y- -y_~~~ - - -9

-------

cOil 15cQJ

000 10~~5 050Z

000

800

eo 700~~ 600pound 500eiJcCJ 400V)

0 300~~ 200

100o

o 200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

20

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

6 Effeet of pressure on yield strength of variousbee metals GS grain size

--0 Fc GS=11Jlnl 147

-0 Fe GS=14Jlm 147

-[S- Fe GS=19Jlm 147

-83- - Fe GS=30Jlm 147

-- - Fe GS=450~lIn 147

6 - - PM T 72- ungsten

-pound --Arc-Melted Tunsten 72

information for the intermetallic NiAI which possessesa B2 (ie bcc derivative) crystal structure while Fig 8is a plot of data from more recent work on compositesbased on either aluminium or magnesium alloymatrixes The data reported for the control materials(ie no pressure soaking) occur on the ordinate at0middot1 MPa (ie atmospheric pressure) Figures 5a 6a7a and 8a summarise the reported values for theyield strength obtained either during tension testswith superimposed pressure or after pressure soakingat the levels of hydrostatic pressure indicated Figures

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156 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullNill Cast and extruded 161

-[S)- - CP-NiAI Prepressurised 166

-EB - - - HP NAlP d 166- 1 repressunse

- -- - - - NiAI-NPrepressurised 166

50

300

(a)

1500

EB

(b)

middotmiddotlSI

__

middotEB

-bullbull-

bull

1000

-----------

1

500

_------------ --- -_---

Superimposed Hydrostatic Pressure MPa

100

50

20

00

o

c~ 15QJl-rj~ 10~8~ 05Z

oo 500 1000 1500

Superimposed Hydrostatic Pressure MPa

el~~ 200

250

o annealedp ~a~~a p ~a~~a p ~~~aT = 200degC 2h T = 400degC 2h

Strain

(c)d

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure c stress-strain curvesof polycrystalline NiAI tested in tension after annealing at 82JOC for 2 h pressurised to 14 GPa and tested at atmospheric pressure and afteraging pressurised specimens at either 200degC or 400degC for 2 h (Ref 159) (arrows show proportional limit) d dislocations being punched from Zrinclusion in NiAI pressurised to 1middot4 GPa (Refs 156 157 160 161)

7 Effect of pressure on yield strength of NiAI

of dislocations and a slight increase in the yieldstrength because of work hardening Little effect ofpressurisation was 0bserved on higher strengthPowder metallurgy produced NiAI (cf Fig7a

International Materials Reviews 1998 Vol 43 No4

and b)166 or W as well as arc-melted W (cf Fig6aand b) 72 in part due to the higher strengths of thematerials tested and the limited range of pressuresutilised

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 157

500

600(a)

Effects of pressure on work hardeningexponent nThe effects of testing with superimposed pressureon the work hardening exponent n have beeninfrequently studied Figure 9a and b illustrates theexperimentally measured effect of superimposed press-ure on n for a high strength aluminium alloy(7075- T651) tested in different orientations withrespect to the rolling direction Testing was conductedwith superimposed pressure on either uniaxial tensionspecimens or plane strain tension specimens andgenerally revealed an increase in n with increasingpressure The authors5051 indicated that such obser-vations could be related to the amount of secondphase particles which could punch out dislocationloops because of their smaller compressibility in amanner analogous to that described above for thecomposite materials

yield stress apparently arises because of pressureinduced dislocation generation around the reinforce-ment which increases significantly the local dislo-cation density thereby providing local hardening anda higher yield strength192195196 Transmission elec-tron microscope studies have confirmed that suchevents can occur provided the pressurisation is con-ducted at a large enough pressure to generate shearstresses of sufficient magnitude near the reinforce-ment192 Testing with superimposed pressure has alsobeen shown to inhibit the accumulation of damage(eg void initiation and growth) in such materials Asthe accumulation of damage reduces the load bearingarea and instantaneous modulus in such compositesand thereby reduces the strain hardening rate press-ure induced damage suppression has been proposedas also contributing to the elevated flow stressesobtained during tests conducted with superimposedpressure192196201 This point is further discussedbelow when summarising the effects of confiningpressure on the UTS In addition recent work hasalso shown that the level of residual stress in thematrix and reinforcement can be changed via pressur-isation343344 Finally various models315-320 have indi-cated that the presence of the non-deformingreinforcement particles provides constrained flow andenhances the flow stress of the matrix The super-position of pressure during tension testing shouldcounteract this effect as illustrated in a fewpapers318-320

15001000

== 0---

~ - - - ---= = = t0- -- - -

(b)

500Superimposed Hydrostatic Pressure MPa

oo

20

EZ 05-

- --6--- 2014AI-20SiCp 13 Jlm-AE 152201

-J - - 2014AI-20SiCp 13 Jlm-T6 152201

-1- - - 2124AI-14SiCw 1 Jlrn-UA 152201

-T---- 2124AI-14SiCw 1 ~m-OA 152201

-X - AI-AI Ni l~m 1523

0-- IIOOAJ-IOAI)O_~ 193

ltgt 193- -- 1100AI-15Al)0 -

- -0- - - 6061AI-15AJ 0 13lrn-UA 1952 3

-- -0- -- 6061AI-15AI 0 (13lm-OA 1952 3

- - -[SJ- - - 6061AI-15At) 0 13~ln-UA 185_ 3

- - -EB- - - 6090AI-25SiCp-SA 193

- - -- - - 6090AI-25SiCp-T6 193

-0- AZ91-19SiCp 15~lTn-T6 193

-e- AZ91-20SiCp52-lIn-T6 J93

c ~~~1-~ 200l x~ -X- X- y

100

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

8 Effect of pressure on yield strength ofdiscontinuously reinforced metal matrixcomposites

The largest changes in the yield strength obtainedeither after pressurisation or during tests with super-imposed pressure have been exhibited by compositematerials as shown in Fig 8a and b (Refs 152 185191-196 198 200 201) One source of the enhanced

Superimposed Hydrostatic Pressure MPa

00o 500 1000 1500 Effects of pressure on UTS

The experimental data for the UTS obtained viatension testing with a range of superimposed pressuresare provided for both monolithic metals as well ascomposites in Figs 10-15 As indicated above thestress state at the UTS (ie before necking) in suchspecimens consists of the uniaxial stress plus anysuperimposed hydrostatic pressure Data obtainedfrom some of Bridgmans original works are providedin Figs 10-13 for a variety of ferrous based systemsheat treated to different strength levels and micro-structures Figure 14a summarises similar data for avariety of other ferrous and non-ferrous structuralmaterials Figure 14b provides the ratio of the UTS

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158 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-6- _ TR uniaxialmiddotmiddotAmiddot TR plane strain-0 --- TW uniaxial

----e TW plane strain-0 - WRuniaxialbull - WRplanc strain

- --0 RW uniaxial- -+- - RW plane strain

-fSJ- Fe-034C-O75Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-045C-O83Mn-OO l6P-O035S-O19Si (as-received)

o normalised l650degF---0 annealed fine-grained- -6- annealed coarse-grained

- - - - - brine-quenchedtenlpered 600degF- - -+- - - brine-quenchedtempered 600degF-- -bull- - -- brine-quenchedtempered 900degF

015 3000

3000

middot11bull

1500 2000 25001000500Superimposed Hydrostatic Pressure MPa

o-- -0--

-6---e----+- -

--SJ-- Fe-O68C-O 7lMn-OO l3P-O025S-O19Si (as-received)

----0 --- Fe-O9C-O47Mn-O015P-O036S-OllSi (as-received)normalised 1650degFannealed fine-grainedannealed coarse-grainedbrine-quenchedspherodisedbrine-quenchedtempered 600degFbrine-quenchedtenlpered 900degF

bullbullbull

oo

2500

500

ce~E 1500rrJ~J 1000

10 Effect of pressure on UTS of various steelstested by Bridgman36

600

(a)

500 600

500

IImiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

middot0-middot -0

400

400

0

300

300

200

200

(b)

100

100Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

bullbull - A R bullbull

~ bull ~

000o

= 200Q)

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o

a n v hydrostatic pressure b normalised n v superimposedhydrostatic pressure

9 Effect of pressure on strain hardening exponentn of 7075AI- T651 (Refs 50 51)

3000

11 Effect of pressure on UTS of various steelstested by Bridgman36

Superimposed Hydrostatic Pressure MPa

500o

o -0

1500 2000 2500 30001000500

bullbull middot11II bull

~o Q ~omiddot omiddot

6 middot0middot omiddotmiddotmiddot=ltgt 6

1000

2500

ri1~ 1500J

~ 2000E

obtained at high pressure to that obtained at atmos-pheric pressure and a normalised UTS of 1middot0 indicatesno measurable effect of superimposed pressure onthe UTS The data for the monolithic metalsshown in Figs 10-13 as well as those summar-ised in Fig 14a and b indicate that superimposedpressure generally has a relatively minor effect on theUTS of most monolithic metals though someexceptions are shown Figure 15a and b illustratesthat composite materials often exhibit significantpressure dependent values for the UTS This hasbeen attributed152185189-201 to the pressure inducedsuppression of damage associated with the reinforce-ment and the matrix (eg void initiationgrowthcoalescence) which is covered in more detail in thefollowing sections on fracture behaviour

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 159

Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

A-+

bull -- -

0middot ------ -----()---6 - - - -

-8

iJII

-4-

-8-

---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

-8--- -lt)-

--

1000

5000

4000

C~ 3000~rJ5

2000 l-3~0

o S - - ~ lJS

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

I I I I I Iii I i

- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

3000

2500 -

d )000 f~~ -

~ 1500

~ middot_cmiddot- ~1000 ~_ibullbullbullbullbull~ - - -- - -- --0

s ti

500

12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure llPa

Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

- - -fr-

---]--

----T-

---0--

- - -lS -

------ - --(gt

--+-0-

4340 tempered 3000e 152

4340 tempered 5000e I 52

4340 tempered 7000e 152

01 Tool Steel Hard 152

01 Tool Steel Medium 152

01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

o 2124AI-14SiCw IJlm-UA 152201

bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

-+ Cu-28W 152

- - - -() - - - AI- Al Ni 152-

800

- - - -----------

~z~~~---~-----~bull-----~200

(a)

ts------6---1---------------- ------~

(b)

20

oo 100 WO ~O 400 ~O WO mo WO

Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

05

100

1000

1000

(a)

(b)

800

800600

600400

400

lZ91 19i

200

200Superimposed Hydrostatic Pressure MPa

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot-[H

----- ------0--middot- ----0

------6--- --6- ----------fJ--- --6

-----[S]----- ----[S]

-1-- - - - - - gtJ- - - - - - -Y- - -- - - -I- - - - - - gtJ

- -_~ ~~-~----- ~ _

middotmiddot~~-plusmn~middot~1middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

Superimposed Hydrostatic Pressure MPa

(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

~~ 1500

rJ5~ 1000

500

00

20

1500~~8 10l-o0Z

05

000

categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

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156 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullNill Cast and extruded 161

-[S)- - CP-NiAI Prepressurised 166

-EB - - - HP NAlP d 166- 1 repressunse

- -- - - - NiAI-NPrepressurised 166

50

300

(a)

1500

EB

(b)

middotmiddotlSI

__

middotEB

-bullbull-

bull

1000

-----------

1

500

_------------ --- -_---

Superimposed Hydrostatic Pressure MPa

100

50

20

00

o

c~ 15QJl-rj~ 10~8~ 05Z

oo 500 1000 1500

Superimposed Hydrostatic Pressure MPa

el~~ 200

250

o annealedp ~a~~a p ~a~~a p ~~~aT = 200degC 2h T = 400degC 2h

Strain

(c)d

a yield strength v superimposed hydrostatic pressure b normalised yield strength v superimposed hydrostatic pressure c stress-strain curvesof polycrystalline NiAI tested in tension after annealing at 82JOC for 2 h pressurised to 14 GPa and tested at atmospheric pressure and afteraging pressurised specimens at either 200degC or 400degC for 2 h (Ref 159) (arrows show proportional limit) d dislocations being punched from Zrinclusion in NiAI pressurised to 1middot4 GPa (Refs 156 157 160 161)

7 Effect of pressure on yield strength of NiAI

of dislocations and a slight increase in the yieldstrength because of work hardening Little effect ofpressurisation was 0bserved on higher strengthPowder metallurgy produced NiAI (cf Fig7a

International Materials Reviews 1998 Vol 43 No4

and b)166 or W as well as arc-melted W (cf Fig6aand b) 72 in part due to the higher strengths of thematerials tested and the limited range of pressuresutilised

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 157

500

600(a)

Effects of pressure on work hardeningexponent nThe effects of testing with superimposed pressureon the work hardening exponent n have beeninfrequently studied Figure 9a and b illustrates theexperimentally measured effect of superimposed press-ure on n for a high strength aluminium alloy(7075- T651) tested in different orientations withrespect to the rolling direction Testing was conductedwith superimposed pressure on either uniaxial tensionspecimens or plane strain tension specimens andgenerally revealed an increase in n with increasingpressure The authors5051 indicated that such obser-vations could be related to the amount of secondphase particles which could punch out dislocationloops because of their smaller compressibility in amanner analogous to that described above for thecomposite materials

yield stress apparently arises because of pressureinduced dislocation generation around the reinforce-ment which increases significantly the local dislo-cation density thereby providing local hardening anda higher yield strength192195196 Transmission elec-tron microscope studies have confirmed that suchevents can occur provided the pressurisation is con-ducted at a large enough pressure to generate shearstresses of sufficient magnitude near the reinforce-ment192 Testing with superimposed pressure has alsobeen shown to inhibit the accumulation of damage(eg void initiation and growth) in such materials Asthe accumulation of damage reduces the load bearingarea and instantaneous modulus in such compositesand thereby reduces the strain hardening rate press-ure induced damage suppression has been proposedas also contributing to the elevated flow stressesobtained during tests conducted with superimposedpressure192196201 This point is further discussedbelow when summarising the effects of confiningpressure on the UTS In addition recent work hasalso shown that the level of residual stress in thematrix and reinforcement can be changed via pressur-isation343344 Finally various models315-320 have indi-cated that the presence of the non-deformingreinforcement particles provides constrained flow andenhances the flow stress of the matrix The super-position of pressure during tension testing shouldcounteract this effect as illustrated in a fewpapers318-320

15001000

== 0---

~ - - - ---= = = t0- -- - -

(b)

500Superimposed Hydrostatic Pressure MPa

oo

20

EZ 05-

- --6--- 2014AI-20SiCp 13 Jlm-AE 152201

-J - - 2014AI-20SiCp 13 Jlm-T6 152201

-1- - - 2124AI-14SiCw 1 Jlrn-UA 152201

-T---- 2124AI-14SiCw 1 ~m-OA 152201

-X - AI-AI Ni l~m 1523

0-- IIOOAJ-IOAI)O_~ 193

ltgt 193- -- 1100AI-15Al)0 -

- -0- - - 6061AI-15AJ 0 13lrn-UA 1952 3

-- -0- -- 6061AI-15AI 0 (13lm-OA 1952 3

- - -[SJ- - - 6061AI-15At) 0 13~ln-UA 185_ 3

- - -EB- - - 6090AI-25SiCp-SA 193

- - -- - - 6090AI-25SiCp-T6 193

-0- AZ91-19SiCp 15~lTn-T6 193

-e- AZ91-20SiCp52-lIn-T6 J93

c ~~~1-~ 200l x~ -X- X- y

100

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

8 Effect of pressure on yield strength ofdiscontinuously reinforced metal matrixcomposites

The largest changes in the yield strength obtainedeither after pressurisation or during tests with super-imposed pressure have been exhibited by compositematerials as shown in Fig 8a and b (Refs 152 185191-196 198 200 201) One source of the enhanced

Superimposed Hydrostatic Pressure MPa

00o 500 1000 1500 Effects of pressure on UTS

The experimental data for the UTS obtained viatension testing with a range of superimposed pressuresare provided for both monolithic metals as well ascomposites in Figs 10-15 As indicated above thestress state at the UTS (ie before necking) in suchspecimens consists of the uniaxial stress plus anysuperimposed hydrostatic pressure Data obtainedfrom some of Bridgmans original works are providedin Figs 10-13 for a variety of ferrous based systemsheat treated to different strength levels and micro-structures Figure 14a summarises similar data for avariety of other ferrous and non-ferrous structuralmaterials Figure 14b provides the ratio of the UTS

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158 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-6- _ TR uniaxialmiddotmiddotAmiddot TR plane strain-0 --- TW uniaxial

----e TW plane strain-0 - WRuniaxialbull - WRplanc strain

- --0 RW uniaxial- -+- - RW plane strain

-fSJ- Fe-034C-O75Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-045C-O83Mn-OO l6P-O035S-O19Si (as-received)

o normalised l650degF---0 annealed fine-grained- -6- annealed coarse-grained

- - - - - brine-quenchedtenlpered 600degF- - -+- - - brine-quenchedtempered 600degF-- -bull- - -- brine-quenchedtempered 900degF

015 3000

3000

middot11bull

1500 2000 25001000500Superimposed Hydrostatic Pressure MPa

o-- -0--

-6---e----+- -

--SJ-- Fe-O68C-O 7lMn-OO l3P-O025S-O19Si (as-received)

----0 --- Fe-O9C-O47Mn-O015P-O036S-OllSi (as-received)normalised 1650degFannealed fine-grainedannealed coarse-grainedbrine-quenchedspherodisedbrine-quenchedtempered 600degFbrine-quenchedtenlpered 900degF

bullbullbull

oo

2500

500

ce~E 1500rrJ~J 1000

10 Effect of pressure on UTS of various steelstested by Bridgman36

600

(a)

500 600

500

IImiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

middot0-middot -0

400

400

0

300

300

200

200

(b)

100

100Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

bullbull - A R bullbull

~ bull ~

000o

= 200Q)

=oc0lt

~ 150~=2

Q)C

100tt==~ 050eoZ 000

o

a n v hydrostatic pressure b normalised n v superimposedhydrostatic pressure

9 Effect of pressure on strain hardening exponentn of 7075AI- T651 (Refs 50 51)

3000

11 Effect of pressure on UTS of various steelstested by Bridgman36

Superimposed Hydrostatic Pressure MPa

500o

o -0

1500 2000 2500 30001000500

bullbull middot11II bull

~o Q ~omiddot omiddot

6 middot0middot omiddotmiddotmiddot=ltgt 6

1000

2500

ri1~ 1500J

~ 2000E

obtained at high pressure to that obtained at atmos-pheric pressure and a normalised UTS of 1middot0 indicatesno measurable effect of superimposed pressure onthe UTS The data for the monolithic metalsshown in Figs 10-13 as well as those summar-ised in Fig 14a and b indicate that superimposedpressure generally has a relatively minor effect on theUTS of most monolithic metals though someexceptions are shown Figure 15a and b illustratesthat composite materials often exhibit significantpressure dependent values for the UTS This hasbeen attributed152185189-201 to the pressure inducedsuppression of damage associated with the reinforce-ment and the matrix (eg void initiationgrowthcoalescence) which is covered in more detail in thefollowing sections on fracture behaviour

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 159

Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

A-+

bull -- -

0middot ------ -----()---6 - - - -

-8

iJII

-4-

-8-

---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

-8--- -lt)-

--

1000

5000

4000

C~ 3000~rJ5

2000 l-3~0

o S - - ~ lJS

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

I I I I I Iii I i

- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

3000

2500 -

d )000 f~~ -

~ 1500

~ middot_cmiddot- ~1000 ~_ibullbullbullbullbull~ - - -- - -- --0

s ti

500

12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure llPa

Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

- - -fr-

---]--

----T-

---0--

- - -lS -

------ - --(gt

--+-0-

4340 tempered 3000e 152

4340 tempered 5000e I 52

4340 tempered 7000e 152

01 Tool Steel Hard 152

01 Tool Steel Medium 152

01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

o 2124AI-14SiCw IJlm-UA 152201

bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

-+ Cu-28W 152

- - - -() - - - AI- Al Ni 152-

800

- - - -----------

~z~~~---~-----~bull-----~200

(a)

ts------6---1---------------- ------~

(b)

20

oo 100 WO ~O 400 ~O WO mo WO

Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

05

100

1000

1000

(a)

(b)

800

800600

600400

400

lZ91 19i

200

200Superimposed Hydrostatic Pressure MPa

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot-[H

----- ------0--middot- ----0

------6--- --6- ----------fJ--- --6

-----[S]----- ----[S]

-1-- - - - - - gtJ- - - - - - -Y- - -- - - -I- - - - - - gtJ

- -_~ ~~-~----- ~ _

middotmiddot~~-plusmn~middot~1middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

Superimposed Hydrostatic Pressure MPa

(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

~~ 1500

rJ5~ 1000

500

00

20

1500~~8 10l-o0Z

05

000

categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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500

600(a)

Effects of pressure on work hardeningexponent nThe effects of testing with superimposed pressureon the work hardening exponent n have beeninfrequently studied Figure 9a and b illustrates theexperimentally measured effect of superimposed press-ure on n for a high strength aluminium alloy(7075- T651) tested in different orientations withrespect to the rolling direction Testing was conductedwith superimposed pressure on either uniaxial tensionspecimens or plane strain tension specimens andgenerally revealed an increase in n with increasingpressure The authors5051 indicated that such obser-vations could be related to the amount of secondphase particles which could punch out dislocationloops because of their smaller compressibility in amanner analogous to that described above for thecomposite materials

yield stress apparently arises because of pressureinduced dislocation generation around the reinforce-ment which increases significantly the local dislo-cation density thereby providing local hardening anda higher yield strength192195196 Transmission elec-tron microscope studies have confirmed that suchevents can occur provided the pressurisation is con-ducted at a large enough pressure to generate shearstresses of sufficient magnitude near the reinforce-ment192 Testing with superimposed pressure has alsobeen shown to inhibit the accumulation of damage(eg void initiation and growth) in such materials Asthe accumulation of damage reduces the load bearingarea and instantaneous modulus in such compositesand thereby reduces the strain hardening rate press-ure induced damage suppression has been proposedas also contributing to the elevated flow stressesobtained during tests conducted with superimposedpressure192196201 This point is further discussedbelow when summarising the effects of confiningpressure on the UTS In addition recent work hasalso shown that the level of residual stress in thematrix and reinforcement can be changed via pressur-isation343344 Finally various models315-320 have indi-cated that the presence of the non-deformingreinforcement particles provides constrained flow andenhances the flow stress of the matrix The super-position of pressure during tension testing shouldcounteract this effect as illustrated in a fewpapers318-320

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EZ 05-

- --6--- 2014AI-20SiCp 13 Jlm-AE 152201

-J - - 2014AI-20SiCp 13 Jlm-T6 152201

-1- - - 2124AI-14SiCw 1 Jlrn-UA 152201

-T---- 2124AI-14SiCw 1 ~m-OA 152201

-X - AI-AI Ni l~m 1523

0-- IIOOAJ-IOAI)O_~ 193

ltgt 193- -- 1100AI-15Al)0 -

- -0- - - 6061AI-15AJ 0 13lrn-UA 1952 3

-- -0- -- 6061AI-15AI 0 (13lm-OA 1952 3

- - -[SJ- - - 6061AI-15At) 0 13~ln-UA 185_ 3

- - -EB- - - 6090AI-25SiCp-SA 193

- - -- - - 6090AI-25SiCp-T6 193

-0- AZ91-19SiCp 15~lTn-T6 193

-e- AZ91-20SiCp52-lIn-T6 J93

c ~~~1-~ 200l x~ -X- X- y

100

a yield strength v superimposed hydrostatic pressure b normalisedyield strength v superimposed hydrostatic pressure

8 Effect of pressure on yield strength ofdiscontinuously reinforced metal matrixcomposites

The largest changes in the yield strength obtainedeither after pressurisation or during tests with super-imposed pressure have been exhibited by compositematerials as shown in Fig 8a and b (Refs 152 185191-196 198 200 201) One source of the enhanced

Superimposed Hydrostatic Pressure MPa

00o 500 1000 1500 Effects of pressure on UTS

The experimental data for the UTS obtained viatension testing with a range of superimposed pressuresare provided for both monolithic metals as well ascomposites in Figs 10-15 As indicated above thestress state at the UTS (ie before necking) in suchspecimens consists of the uniaxial stress plus anysuperimposed hydrostatic pressure Data obtainedfrom some of Bridgmans original works are providedin Figs 10-13 for a variety of ferrous based systemsheat treated to different strength levels and micro-structures Figure 14a summarises similar data for avariety of other ferrous and non-ferrous structuralmaterials Figure 14b provides the ratio of the UTS

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158 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-6- _ TR uniaxialmiddotmiddotAmiddot TR plane strain-0 --- TW uniaxial

----e TW plane strain-0 - WRuniaxialbull - WRplanc strain

- --0 RW uniaxial- -+- - RW plane strain

-fSJ- Fe-034C-O75Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-045C-O83Mn-OO l6P-O035S-O19Si (as-received)

o normalised l650degF---0 annealed fine-grained- -6- annealed coarse-grained

- - - - - brine-quenchedtenlpered 600degF- - -+- - - brine-quenchedtempered 600degF-- -bull- - -- brine-quenchedtempered 900degF

015 3000

3000

middot11bull

1500 2000 25001000500Superimposed Hydrostatic Pressure MPa

o-- -0--

-6---e----+- -

--SJ-- Fe-O68C-O 7lMn-OO l3P-O025S-O19Si (as-received)

----0 --- Fe-O9C-O47Mn-O015P-O036S-OllSi (as-received)normalised 1650degFannealed fine-grainedannealed coarse-grainedbrine-quenchedspherodisedbrine-quenchedtempered 600degFbrine-quenchedtenlpered 900degF

bullbullbull

oo

2500

500

ce~E 1500rrJ~J 1000

10 Effect of pressure on UTS of various steelstested by Bridgman36

600

(a)

500 600

500

IImiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

middot0-middot -0

400

400

0

300

300

200

200

(b)

100

100Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

bullbull - A R bullbull

~ bull ~

000o

= 200Q)

=oc0lt

~ 150~=2

Q)C

100tt==~ 050eoZ 000

o

a n v hydrostatic pressure b normalised n v superimposedhydrostatic pressure

9 Effect of pressure on strain hardening exponentn of 7075AI- T651 (Refs 50 51)

3000

11 Effect of pressure on UTS of various steelstested by Bridgman36

Superimposed Hydrostatic Pressure MPa

500o

o -0

1500 2000 2500 30001000500

bullbull middot11II bull

~o Q ~omiddot omiddot

6 middot0middot omiddotmiddotmiddot=ltgt 6

1000

2500

ri1~ 1500J

~ 2000E

obtained at high pressure to that obtained at atmos-pheric pressure and a normalised UTS of 1middot0 indicatesno measurable effect of superimposed pressure onthe UTS The data for the monolithic metalsshown in Figs 10-13 as well as those summar-ised in Fig 14a and b indicate that superimposedpressure generally has a relatively minor effect on theUTS of most monolithic metals though someexceptions are shown Figure 15a and b illustratesthat composite materials often exhibit significantpressure dependent values for the UTS This hasbeen attributed152185189-201 to the pressure inducedsuppression of damage associated with the reinforce-ment and the matrix (eg void initiationgrowthcoalescence) which is covered in more detail in thefollowing sections on fracture behaviour

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Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

A-+

bull -- -

0middot ------ -----()---6 - - - -

-8

iJII

-4-

-8-

---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

-8--- -lt)-

--

1000

5000

4000

C~ 3000~rJ5

2000 l-3~0

o S - - ~ lJS

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

I I I I I Iii I i

- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

3000

2500 -

d )000 f~~ -

~ 1500

~ middot_cmiddot- ~1000 ~_ibullbullbullbullbull~ - - -- - -- --0

s ti

500

12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure llPa

Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

- - -fr-

---]--

----T-

---0--

- - -lS -

------ - --(gt

--+-0-

4340 tempered 3000e 152

4340 tempered 5000e I 52

4340 tempered 7000e 152

01 Tool Steel Hard 152

01 Tool Steel Medium 152

01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

o 2124AI-14SiCw IJlm-UA 152201

bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

-+ Cu-28W 152

- - - -() - - - AI- Al Ni 152-

800

- - - -----------

~z~~~---~-----~bull-----~200

(a)

ts------6---1---------------- ------~

(b)

20

oo 100 WO ~O 400 ~O WO mo WO

Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

05

100

1000

1000

(a)

(b)

800

800600

600400

400

lZ91 19i

200

200Superimposed Hydrostatic Pressure MPa

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot-[H

----- ------0--middot- ----0

------6--- --6- ----------fJ--- --6

-----[S]----- ----[S]

-1-- - - - - - gtJ- - - - - - -Y- - -- - - -I- - - - - - gtJ

- -_~ ~~-~----- ~ _

middotmiddot~~-plusmn~middot~1middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

Superimposed Hydrostatic Pressure MPa

(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

~~ 1500

rJ5~ 1000

500

00

20

1500~~8 10l-o0Z

05

000

categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

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fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

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structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

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390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

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158 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-6- _ TR uniaxialmiddotmiddotAmiddot TR plane strain-0 --- TW uniaxial

----e TW plane strain-0 - WRuniaxialbull - WRplanc strain

- --0 RW uniaxial- -+- - RW plane strain

-fSJ- Fe-034C-O75Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-045C-O83Mn-OO l6P-O035S-O19Si (as-received)

o normalised l650degF---0 annealed fine-grained- -6- annealed coarse-grained

- - - - - brine-quenchedtenlpered 600degF- - -+- - - brine-quenchedtempered 600degF-- -bull- - -- brine-quenchedtempered 900degF

015 3000

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1500 2000 25001000500Superimposed Hydrostatic Pressure MPa

o-- -0--

-6---e----+- -

--SJ-- Fe-O68C-O 7lMn-OO l3P-O025S-O19Si (as-received)

----0 --- Fe-O9C-O47Mn-O015P-O036S-OllSi (as-received)normalised 1650degFannealed fine-grainedannealed coarse-grainedbrine-quenchedspherodisedbrine-quenchedtempered 600degFbrine-quenchedtenlpered 900degF

bullbullbull

oo

2500

500

ce~E 1500rrJ~J 1000

10 Effect of pressure on UTS of various steelstested by Bridgman36

600

(a)

500 600

500

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middot0-middot -0

400

400

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300

300

200

200

(b)

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100Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

bullbull - A R bullbull

~ bull ~

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= 200Q)

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Q)C

100tt==~ 050eoZ 000

o

a n v hydrostatic pressure b normalised n v superimposedhydrostatic pressure

9 Effect of pressure on strain hardening exponentn of 7075AI- T651 (Refs 50 51)

3000

11 Effect of pressure on UTS of various steelstested by Bridgman36

Superimposed Hydrostatic Pressure MPa

500o

o -0

1500 2000 2500 30001000500

bullbull middot11II bull

~o Q ~omiddot omiddot

6 middot0middot omiddotmiddotmiddot=ltgt 6

1000

2500

ri1~ 1500J

~ 2000E

obtained at high pressure to that obtained at atmos-pheric pressure and a normalised UTS of 1middot0 indicatesno measurable effect of superimposed pressure onthe UTS The data for the monolithic metalsshown in Figs 10-13 as well as those summar-ised in Fig 14a and b indicate that superimposedpressure generally has a relatively minor effect on theUTS of most monolithic metals though someexceptions are shown Figure 15a and b illustratesthat composite materials often exhibit significantpressure dependent values for the UTS This hasbeen attributed152185189-201 to the pressure inducedsuppression of damage associated with the reinforce-ment and the matrix (eg void initiationgrowthcoalescence) which is covered in more detail in thefollowing sections on fracture behaviour

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 159

Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

A-+

bull -- -

0middot ------ -----()---6 - - - -

-8

iJII

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-8-

---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

-8--- -lt)-

--

1000

5000

4000

C~ 3000~rJ5

2000 l-3~0

o S - - ~ lJS

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

I I I I I Iii I i

- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

3000

2500 -

d )000 f~~ -

~ 1500

~ middot_cmiddot- ~1000 ~_ibullbullbullbullbull~ - - -- - -- --0

s ti

500

12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure llPa

Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

- - -fr-

---]--

----T-

---0--

- - -lS -

------ - --(gt

--+-0-

4340 tempered 3000e 152

4340 tempered 5000e I 52

4340 tempered 7000e 152

01 Tool Steel Hard 152

01 Tool Steel Medium 152

01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

o 2124AI-14SiCw IJlm-UA 152201

bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

-+ Cu-28W 152

- - - -() - - - AI- Al Ni 152-

800

- - - -----------

~z~~~---~-----~bull-----~200

(a)

ts------6---1---------------- ------~

(b)

20

oo 100 WO ~O 400 ~O WO mo WO

Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

05

100

1000

1000

(a)

(b)

800

800600

600400

400

lZ91 19i

200

200Superimposed Hydrostatic Pressure MPa

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot-[H

----- ------0--middot- ----0

------6--- --6- ----------fJ--- --6

-----[S]----- ----[S]

-1-- - - - - - gtJ- - - - - - -Y- - -- - - -I- - - - - - gtJ

- -_~ ~~-~----- ~ _

middotmiddot~~-plusmn~middot~1middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot

Superimposed Hydrostatic Pressure MPa

(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

~~ 1500

rJ5~ 1000

500

00

20

1500~~8 10l-o0Z

05

000

categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 159

Abull

]

6 -6 middotmiddot-middotmiddot-0

--0--0

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bull -- -

0middot ------ -----()---6 - - - -

-8

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---R Fc-O 094C-O 3 61v1n-O 02P - () 02 25-O35Si-1226Cr-()46Ni-O5~10las- rccei ved)F c-O 067 C-O 05IVI n-O 02P -003 S-051 Si-1749Cr-041 Ni(as-received)Fe-O058C-O 7Tvln-O03P-OO 13S-08551-1851 Cr-895Ni-O2Cu(as-received)

-- -+ --- Fe-OOSl C-OS9Mn-O03P-O02S-O47Si-1831 Cr-lO27Ni-O2Cu(as-received)High-carbon Steels 48HRC51HRC56HRC60HRC63HRC

-- -0-- -0--

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o S - - ~ lJS

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- - -IS- -Fe-O55C-O35Tvln-O04P-O04S-O20Si-345Ni-23Cr las-received

-- -0 -- Fc-O3C-O18Ir1n-OO 11P-O02S-O20Si-298Ni-l18Cr las-received)

-- -0 Fe-O26C-O23Mn-O02P-O025S-O06Si-304Ni-l4Cr (as-received)

ltgt - - Fc-O3C-O24Ir1n-O024P-O03 IS-O20Si-296Ni-I29Cr las-received)

-6- - - - 1045 Steel (as-received)- - - - - F~-O6C-( 71tln-Oc)3P-O03S-1 9Si

(ai-receivcd)- - - -R oil-quenched

oo

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12 Effect of pressure on UTS of various steelstested by Bridgman36

oo 500 1000 1500 2000 2500 3000

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Effects of superimposed pressure onfracture behaviourGeneral effects of stress state on fractureChanges in stress state have been shown to exertcontrolling effects on the fracture behaviour of mater-ials and can induce a ductile to brittle (or vice versa)transition in some systems Detailed descriptions ofthe various microstructural factors controlling suchevents is beyond the scope of this review Readersinterested in such details are referred to specificarticles and books for the topic of interest345-350However it is important to highlight some of the keyfeatures which distinguish the micromechanisms offracture which operate in materials that fail via ductile(eg microvoid coalescence) fracture from those thatfail via brittle (eg cleavage) fracture Figure 16 showsschematically the principal types of fracture mechan-isms typically observed in metallic based systems Themicro mechanical fracture models which have beendeveloped using experimental input reveal that thepressure sensitivity of such fracture micromechanismsare distinctly different as outlined below In generaldeformation and fracture micromechanisms which areassociated with positive volume changes are categor-ised as dilatant processes and should exhibit highlypressure dependent behaviour In contrast pres-sure independent behaviour would be expected fordeformation and fracture processes predominantlycontrolled by deviatoric stresses as was shown abovefor the case of yielding in homogeneous isotropicmaterials

13 Effect of pressure on UTS of various steelstested by Bridgman36

Stresses controlling brittle fractureBrittle fracture in this context refers to the fractureappearance and micromechanisms which produce fail-ure at low macroscopic strains at low homologoustemperatures Such brittle fracture may occur eithertransgranularly via transgranular cleavage fracture(Figs 16a and 17a) or via brittle intergranular separa-tion (Figs 16b and 17b) Comparatively greater effortshave been expended on modelling and experimentallyevaluating the factors controlling brittle cleavage frac-ture in comparison with brittle intergranular fractureHowever many of the issues regarding the effects ofchanges in stress state on cleavage and intergranularfracture are similar with respect to the present contextwhich treats the effects of stress state on the fracturenucleation event as separate from that of the propa-gation of the crack

A variety of textbooks and articles are availablewhich discuss the factors controlling cleavage fracturein crystalline materials34634734935o In experimentson metallic materials it was often shown that thebrittle fracture stress obtained in uniaxial tensiontests was equivalent to the yield stress in com-pression355 In addition to indicating that someamount of plastic flow typically precedes brittle frac-ture in metallic systems such results also suggestedthe existence of a strong effect of stress state on brittlefracture Brittle fracture in metallic materials is often

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

-0- - 2124AI-UA 152

-e- 2124AI-OA 152

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01 Tool Steel Soft 152

Ti-V Steel 9500e FRT 152

Ti-V Steel 7000e FRT 152

2014AI-T6152

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bull 2124AI-14SiCw IJlm-OA 152201

middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6middotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot2014 Al- 20S iCp 13Jlrn _AE 152

------ 20 14AI-20SiCp 13~tn1-T6 152

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Superimposed Hydrostatic Pressure MPa

00o 100 200 300 400 500 600 700 800

Superimposed Hydrostatic Pressure MPa

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

1500~~8 10l-o0Z

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100

1000

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(b)

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800600

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400

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200

200Superimposed Hydrostatic Pressure MPa

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(8)

a UTS v superimposed hydrostatic pressure b normalised UTS vsuperimposed hydrostatic pressure

14 Effect of pressure on UTS of various metals

2500

2000

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500

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20

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categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

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10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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345 P F THOMASON Ductile fracture of metals 1990 New YorkPergamon Press

346 J F KNOTT Fundamentals of fracture mechanics 1973London Butterworths

347 A W THOMPSON and J F KNOTT Metall Trans A 199324A523

348 R O RITCHIE and A W THOMPSON Metall Trans A 198516A233

349 F A McCLINTOCK and A S ARGON Mechanical behaviour ofmaterials 1966 Reading MA Addison-Wesley

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351 M F ASHBY J D EMBURY S H COOKSLEY and D TEIRLINCK

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materials 1998 Upper Saddle River NJ Prentice Hall353 A SAMANT and 1 1 LEWANDOWSKI Metall Mater Trans A

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Strength of metals and alloys - ICSMA 7 Montreal Aug1985 1193 1985 New York Pergamon Press

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356 A N STROH Adv Phys 1957 6418357 A N STROH Phios Mag 1958 3 597358 1 FREIDEL Dislocations 1964 New York Pergamon Press359 1 F KNOTT and A H COTTRELL J Iron Steel Inst 1963

201249360 J F K~OTT J Iron Steel Inst 1966 204 104361 1 F KOTT J Iron Steel lISt 1966 204 1014362 J F K~OTT J Iron Steel Inst 1967 205 288363 OROWAN Trans Inst Eng Shipbuilders Scotland 194589 1165364 N N DAVIDENKOV Dinamicheskaya ispytania metallov 1936

Moscow USSR365 1 1 LEWANDOWSKI and A W THOMPSON Metall Trans 1986

17A 1769366 J J LEWANDOWSKI and A W THOMPSON Acta Metall 1987

35 1453367 A SAMANT and 1 J LEWANDOWSKI Metall Mater Trans A

1997 28A 389368 D TEIRLINCK F ZOK J D EMBURY and M F ASHBY Acta

Metall 1988 36 1213369 D TEIRLINCK M F ASHBY and J D EMBURY in Advances in

fracture research - ICF 6 New Delhi India Dec 1984 105New York Pergamon Press

370 w M GARRISON Jr and N R MOODY J Phys Chem Solids1987 48 1035

371 A W THOMPSON Metall Trans A 1987 18A 1877372 L M BROWN and J D EMBURY in Proc 3rd Int Conf on

Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

374 s H GOOD and L M BROWN Acta Metall 197927 1375 L M BROWN and w M STOBBS Phios Mag 197634 351376 P F THOMASON Ductile fracture of metals 94 1990 New

York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

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160 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

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15 Effect of pressure on UTS of discontinuouslyreinforced metal matrix composites

Brittle fracture which occurs under such conditionsshould be pressure independent because fracturenucleation is assumed coincident with yielding whichitself is typically pressure independent Significantpressure induced increases in ductility are notexpected in such cases

In contrast the conditions for propagation con-trolled brittle fracture in metallic materials requiresthat the fracture nucleation event(s) occur easilywith the subsequent propagation of the fracturenuclei considered as the most difficult event346347It has been proposed that the propagation of suchfracture nuclei typically occur by reaching a constantmaximum principal stress359-364 that is temper-ature independent A number of metallic systemsappear to obey such a fracture criterion over awide range of test conditions and test temper-atures350353359-362365-367and indicate that brittlefracture under such conditions can be described by

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categorised as nucleation controlled v propagationcontrolled346347 In the former case the nucleation ofthe crack is considered the most difficult event sothat nucleation is typically followed by catastrophicfracture356-358 Considering that some amount of plas-tic flow is typically required to nucleate such crackssuggests that a condition for nucleation controlledbrittle fracture is

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 161

(11)

to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

(b)

(e)

(a)

(d)(c)

LoadingDirection

a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

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a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

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10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

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50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

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1000

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bullbullbull bull

bull bull~

el~

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~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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to raise the stress to the brittle fracture stress mayeventually trigger another more locally ductile frac-ture mode such as microvoid coalescence as suggestedin recent fracture mechanism maps351368369As dis-cussed below the pressure dependence of such ductilefracture micromechanisms is significantly different tothose described above for controlling brittle fracture

where (Je is the critical cohesive interfacial strength(Jrn the mean normal stress and a the effective stressgiven by equation (1)

Both models predict a dependence of voidnucleation on the mean stress In the case of plastic

International Materials Reviews 1998 Vol 43 NO4

Stresses controlling ductile fractureDuctile fracture in metallic materials occurs viathe nucleation growth and coalescence of voidsand is often referred to as micro void coalescence(MVC)345370-372 In contrast to brittle fracture it istypically a fracture mode that requires high levels ofstrain at atmospheric pressure Significant neckingmay occur while the fracture surface appearanceconsists of microscopic dimples that either impingeor are linked via shear fracture as shown in Figs 16cand 17c The predominant fracture nuclei in suchcases include inclusions carbides other second phaseparticles and grain boundary regions As expectedvoid evolution in such cases does not occur underconstant volume conditions and a significant pressureeffect is expected for materials which fail via MVC

The effects of superimposed pressure on the stressescontrolling MVC are discussed below There area variety of models for void nucleation in MVCas recently reviewed34537o-374 Void nucleation atparticles may occur via particle cracking or via de-cohesion of the particlematrix interface Nucleationcan occur at strainsstresses as low as the yieldstrainstress or at stresses beyond the UTS Bothparticle cracking and interface decohesion have beenmodelled by assuming that a critical tensile stress isrequired either in the particle or at the particlematrixinterface The nucleation condition in such casescould be affected by a superimposed pressure in themanner suggested by Argon et a1373 and Goods andBrown374 Pressures of sufficient magnitude couldcompletely suppress void nucleation Two of the manyavailable models for void nucleation are now reviewedin the light of the potential effect of superposedpressure The Brown and Stobbs dislocation model375for void nucleation at particles with radii less than orequal to 1 Jlm invokes a critical strain Gn to nucleatemicro voids by the decohesion of the particlematrixinterface and is given by

Gn=Krplaquo(Je-(Jrn)2 (10)

where K is a material constant depending on thevolume fraction of particles 1p the particle radius inJlm (Je the critical interfacial cohesive strength of theinterface and (Jrn the mean normal stress given bylaquo(JI + (J2 + (J3)3 Argon et als continuum model373

for void nucleation at particles with radii greater than1 Jlm predicts that the critical condition for particlematrix interface separation is reached when

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a transgranular cleavage b intergranular fracture c microvoidcoalescence or dimpled rupture d ductile rupture e localised shear

16 General categories of fracture processes inmetallic materials351352

the following equation

a=(Jr+P (9)

where (J r is the brittle fracture stress in tension andP the superimposed pressure Brittle fracture undermaximum principal stress control should exhibit afracture stress-superimposed pressure relationshipthat is linear with a slope of 1 Pressure inducedductility increases are expected with such a brittlefracture criterion because of the requirement ofachieving a critical maximum tensile stress and theneed to overcome the superimposed pressure

Finally since it is clear that some amount of plasticflow is required for both crack nucleation and growthin metallic materials it is possible that a transitionfrom nucleation controlled fracture to propagationcontrolled fracture (or vice versa) could occur with asignificant change in stress state For example con-sider the case of significantly increasing the level ofsuperimposed pressure on a material which exhibitsnucleation controlled fracture at low levels of super-imposed hydrostatic pressure This could create acondition where all three principal stresses are com-pressive thereby requiring additional plastic flowwhich would blunt any pre-existing or evolving frac-ture nuclei while requiring additional increases in themaximum principal stress to trigger brittle fracturePressure induced ductility increases in such casesmight be relatively minor at low levels of superim-posed pressure with an abrupt transition at somecritical level of superimposed pressure Sufficientlyhigh levels of superimposed pressure and the resultinghigher levels of strain and work hardening required

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

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162 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

a

b

c

Imm

100 Jlm

~d

e

9

a SEM view of transgranular cleavage fracture surface353 b SEM view of intergranular fracture surface163 c SEM view of microvoid coalescence103d SEM view of ductile rupture 103e SEM view of shear localisation in tension specimen 190 f optical view of shear band in torsion specimen(fracture occurred within intense shear band)354 g etched optical view of shear bands and fracture from notch in precipitation hardened AI alloy354

17 Optical views and SEM fractographs of various fracture processes

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

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Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

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00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

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500 1000 I I 1 I 1

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60

c 50

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a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

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0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

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22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

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Fractured Specimens

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4340 300degC 152

4340 5000C 152

4340 7000C 152

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01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

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ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

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200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

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00~ 30ll~~ 20~

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000

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from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

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60

50

=C 40~~~ 30rBtJcr 20~

00

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00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

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20

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ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

International Materials Reviews 1998 Vol 43 No4

Page 19: Effects of Hydro Static Pressure on Mechanical

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 163

deformation with superposition of a hydrostatic fluidpressure p376 the mean stress (Jm in the above equa-tions is replaced by an effective mean normal stress(Jmerr given by

In this formalism compressive values of P are takento be algebraically negative The Brown and Stobbsdislocation model equation (10) becomes

Gn = Krp((Jc - (Jm - p)2 (13)

while Argon et ais continuum model equation (11)becomes

(Jmerr = (Jm + P (12)

(14)

MVC8689197 Deformation proceeds without MVCto such high strains in these cases that failure occursunder nominally constant volume conditions Thesecond nominally ductile fracture process that is nothighly dilatant involves materials exhibiting intenseshear localisation Fig 16e and 17e Precipitationhardened aluminium alloys heat treated to containshearable precipitates often fail in shear at high valuesof strain in a tension test as shown in Fig 17e (Refs99 189 190 354) or via the propagation of intenseshear bands in torsion354 (cf Fig 17f) or undernotched bend conditions35438o381 Testing with super-imposed pressure might not significantly increaseeither the fracture stress or ductility in such cases

Equations (13) and (14) thus predict an effect ofsuperposed hydrostatic pressure on microvoidnucleation At sufficiently high pressures micro-void nucleation via such a mechanism may beeliminated376

The Rice and Tracey model for void growth ina plastically deforming solid377 and that due toMcCIintock378 similarly shows a large dependence onmean stress The effect of superimposed hydrostaticpressure would be to retard void growth in such casesas reviewed by Thomason376 Finally the effects ofconfining pressure on MVC have been estimated byconsidering a simple plane strain model for the criticalcondition for incipient MVC376 and accounting forthe effect of the superimposed hydrostatic pressure

(In2k( 1 - vi2) = 12 + (Jm2ky + P2ky (15)

where (Jn is the critical value of mean stress requiredto initiate plastic flow or internal necking in theintervoid matrix Vf the volume fraction of microvoidsky the macroscopic shear yield stress and (Jm themean normal stress The superimposed hydrostaticpressure effectively reduces the magnitude of thetensile flow stress and thereby increases the amountof plastic void growth strain required for the coalesc-ence of the voids376 In the case of materials containinga large volume fraction of non-deforming particles(eg discontinuously reinforced composites) it hasbeen demonstrated via finite element analyses thathydrostatic tension evolves in the matrix duringdeformation315-32o379 One of the beneficial effects ofsuperimposed hydrostatic stress would be to counter-act the detrimental hydrostatic tensile stresses whichevolve during deformation in such systems

Void coalescence can occur via void impingementor via shear localisation between voids37o371 Voidimpingement is likely to exhibit a greater pressuresensitivity than shear localisation between voidsbecause of the lower pressure sensitivity of sheardominated processes as described below Regardlessit is generally agreed that the elongation and ductilityare dominated by the strain required for voidnucleation and growth

Although the above discussion indicates that duc-tile fracture typically occurs via highly dilatant pro-cesses that would be expected to exhibit high pressuresensitivity there are two other ductile fracture pro-cesses which are not highly dilatant Consider ductilerupture (Figs 16d and 17d) which occurs under levelsof superimposed pressure sufficient to inhibit

General observations ofductility enhancementPressure induced ductility increases have beenobserved in a variety of monolithic and compositematerials However the magnitude of the ductilityimprovements are not consistent between materialssystems which fracture via different micromechanisms(eg MVC cleavage intergranular shear fracture)while the operative fracture micromechanisms arecontrolled by the microstructure This is due in partto the differences in the pressure dependence of thevarious failure mechanisms listed and discussedabove Data summaries are provided initially followedby a discussion of the magnitude of the pressuredependencies observed

The work of Bridgman36 on a variety of steelsshown in Figs 18-22 reveal a large effect of pressureon the fracture strain obtained from reduction inarea measurements Clear differences between thepressure response were noted and attributed in partto the differences in strength level of the materialsanalysed More recent work on plain carbon steels ofvarying C contents and microstructures are presentedin Fig 23a and b (Refs 75 149) while Fig 24a and b(Refs 63 152) summarise similar work on higheralloy steels with more complicated microstructuresThe values reported for normalised fracture strain inFigs 23b and 24b are the ratio of the fracture strainobtained at high pressure to that obtained at oneatmosphere In some of these cases careful metallo-graphic investigations of cross-sections of fracturedspecimens revealed that the pressure induced ductilitychanges were due to the pressure induced suppressionof damage at various microstructural features includ-ing carbides inclusions grain boundaries and othersecond phase particles Figure 25 redrawn from thework of French and Weinrich87 shows the quantifi-cation of voids associated with cementite particles insteel and clearly shows that increased levels of press-ure inhibit the total number of voids present atequivalent levels of strain Similar results have beenobtained on other spheroidised steels by Brownrigget ai63 as well as on an aluminium alloyl03197reviewed below Figure 26a and b contrasts the ben-eficial effects of superimposed pressure on the fracturestrain of Fe (Ref 149) to that obtained on brittlematerials such as cast iron tungsten magnesiumCu-Bi zinc and a zinc alloy The fracture strain ofFe is large at one atmosphere and highly pressure

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164 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

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Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

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a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

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Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

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4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

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~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

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~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

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20

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CLI GS2011m] 1j8

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ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

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EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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LSImiddot - Fe-O34C-075Mn-O017P-O033S-O18Si (as-received)

- -0 - Fe-OA5C-083Mn-00 16P-0035S-019Si (as-received)

-0 -- normalised 900degC -0 - annealed fine-grained

-6 - - annealed coarse-grained- - bIine-quenched and spheroidised

-- -R bIine-quenchedtempered 315degC-- -+ -- brine-quenchedtempered 315degC-- -bull- - bline-quenchedtelnpered 480degC

5050

-[S Fe-O55C-O35ltln-004P-004Smiddot01] Si-345Ni-23Cr (as-received)

----0 Fe-O3C-018Mn-OO] lP-002S-007Si-298Ni-l18Cr (as-received

o Fe-026C-023Mn-002P-0025S-006Si-394Ni-1ACr (as-received)

ltgt middotFe middotO3C-middotO24Mnmiddot O024P-O031 SmiddotO08Si middot296Nimiddotmiddotl29C (asmiddot--rcceived)

-6- 1045 Steel (as-received) bull Fe-O6C-O7Mn-O03P-l9Si-O03S

annealed-R - - oil-quenched

40

_ - 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

sr

10

00

o1500 2000 2500 30001000500

40

00

o

10

Superimposed Hydrostatic Pressure MPa

18 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

20 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

-rs- Fe-O68C-O711V1n-O013P-O02SS-0 19Si (as-received)

-0 -- Fe-09C-OA7Mn-0015P-O036S-011 Si (as-received)

-0 -- nonnalised 900degC-0 - annealed fine-grained-6- - - annealed coarse-grained

- -- bIine-quenchedspheroidised-- -R brine-quenchedtempered 315degC----+ bIine-quenchedtelnpered 480degC

- - -rsJ 1045 steel (as-received)

- -0 water quenched-0 water quenched 403HRC

-ltgt quenched into salt (il) 425degC 917HRB

middot-Is qucnced into salt (cp 595degC 855HRB

- - - -V- water quenched

- -- - -- ternpered pearlite 258HRCIImiddot tcrnpered Inartensitc 283HRC

50

40 0-lt -~Pc 1 I

~ 30

Ql -c~~ tr~ 20~ -[~J If~

10

00

0 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

21 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

00

bull40

00

o 500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

50

19 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

-bull - Fe-0067C-OOSIvIN-O02P-003S-051 5i-17 49Cr-OAI Ni((ilt-received)

-J- - - Fe-O058C-O70IvlN-O03P-OO 13S-O85Si- 1851 Cr-895Ni-O2Cu((i~-received)

bull Fe-a051 C-O59MN-003P-002S-04751-183] Cr-l O27Ni-O2Cu(as-received)

- -0 High-carbon Steels48HRC

----0 51HRC--8-- 56HRC

----0 60HRC- -- - 63HRC

)( Fe-Oa04C(Ann) 75

~ Fe-OAC(Ann) 75

_middotmiddotmiddotmiddotmiddotmiddotmiddot6 middot--Fe -083 C (nn) 75

-middot--middot0--middotmiddot Fe-I] C(Ann) 75

bull Fe-OAC(Sph) 75

---k--- Fe-OS3C(Sph) 75

II Fc-lIC(Sph) 75

-middotmiddot--0 --- Fc-O02C 149

-[S Fe-O27C 149

-Bmiddot Fe-049C 149

1

1(b) ~

I 1 I 1

2000 250015001 I 1

500 1000 I I 1 I 1

Superimposed Hydrostatic Pressure lIPa

60

c 50

U5Col

-e 30~~E 20oZ

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

23 Effect of pressure on fracture strain of Fe-Calloys

60

Superimposed Hydrostatic Pressure MPa

it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

3000

0

0

bull

middot0

Omiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddotmiddot6~

middot40middotmiddotmiddot

1500 2000 2500

0

1000

IIe

A A

0

500Superimposed Hydrostatic Pressure MPa

50

40c~ 30

I

La tr

~l0

~00

o

22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

A

bullbull

o00

50

CIl

~ 1500~o~ 100c8=z

ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

1045 075JIn Prestrained 63

4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 165

middotRmiddot Fe-O094C-O36f-1N-O023P-O022S-O35Si-1226Cr-046Ni-O5tvl0(as-received)

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it has been clearly shown in various metallographicinvestigations of failed aluminium alloy specimensthat superimposed pressure suppresses damagevoiding associated with inclusion particles Figure29 provides the quantification of the effects of super-imposed pressure on the total void fraction near thefracture surface in 6061AI (Ref 103) and a-brass86while Fig 30a and b illustrates the change in voidshape in 6061AI (Ref 103) that arises due to superim-posed pressure with a transition from high aspectratio voids to smaller nearly spherical voids on going

International Materials Reviews 1998 Vol 43 NO4

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22 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

sensitive because failure is via MVC In contrast castiron 123 tungsten 717274magnesium 74 zinc 112123azincalloy23 and Cu-Bi (Ref 152) re~ain brittle untilsufficient levels of pressure are applied to effect achange in fracture behaviour from one which appar-ently occurs via nucleation control and brittle fractureto a ductile fracture mechanism andor one thatexhibits propagation control This concept is asreviewed elsewhere717274123 while the experimentalevidence is revealed by the abrupt change in fracturestrain v pressure Fig 26a and b The amorphousmetal alloys Pd Cu Si (Ref 323) and Zr Ti Ni Cu Be(Ref 324) fail via intense shear and low ductility at0middot1 MPa (1 atm) and this does not appear to be sig-nificantly affected at moderate pressure levels323324

In addition to the early work conducted on ferrousbase systems a variety of works have focused on non-ferrous systems such as alloys based on aluminiumand copper shown in Fig 27a and b and Fig 28aand b respectively While many of the aluminiumalloys shown in Fig27a and b illustrate a largepressure induced increase in ductility the magnitudeof these increases are clearly alloy and heat treatment(ie microstructure) dependent with pressure inde-pendent behaviour (ie lack of ductility increase withincreasing pressure) exhibited in a number of studiesIn cases where MVC is the operative fracture mode

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

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25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

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Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

(b)

1000

ltgt

800600400

bull bull

200

bullbullbull bull

bull bull~

el~

i ~ltgt

~ ~(a)

200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

10

000

60

d 5000 40~ll 30~~~S 200Z 10-

000

from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

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fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

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390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

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393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

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412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

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Rev 1993 38 193

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166 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

200

25 Number of voids in centre of necked ten-sion specimen tested at various levels ofsuperimposed hydrostatic pressure to theindicated levels of strain e for spheroidisedO5degoe steel (after Ref87)

2520

bull

15

bull

10

Fractured Specimens

amp~t

01 MPa300 MPa

600 MPa

05

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ivlild Steel 118

l045 O75flrn 63

1045 1 4 8Jlln 6~

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4340 300degC 152

4340 5000C 152

4340 7000C 152

01 fool Steel Hard 152

01 Tool Steel Mediunl 15

01 fool Steel Soft 152

Ti-V Steel 950degC FRT 152

Ti- V Steel 700degC FRT 152

o

CJ

o

ltgtbullbull

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

24 Effect of pressure on fracture strain ofvarious steels

posed pressure where MVC was still predominant asshown in Fig 27a and b However a transition topressure independent fracture strains which occurredat higher levels of superimposed pressure (shown inFig27a and b) was coincident with the appearanceof ductile rupture in those studies103123189190alsoconsistent with the discussion above

The modest or lack of ductility increase shownfor a number of the aluminium alloys and heat treat-ments shown in Fig27a and b have been attribu-ted to the lack of pressure dependence of the fail-ure mechanism(s) in such materials For examplethe alloys and heat treatments which exhibit nearlypressure independent ductilities in Fig27a andb include 7075 AI- T4 MB-85-UA and 2124AI_UA99189-191194-196201These alloys and heattreatments fail via an intense localised shear processshown in Figs 16e and 17e-g due to the micro-structural features present in the materials testedSuperimposed hydrostatic pressure at levels well inexcess of the UTS of the material99 do not measurablyaffect the fracture microprocesses or the globalresponse consistent with the discussion above

The effects of alloying additions as well as changesin grain size on the level of pressure induced ductilityincrease for a variety of Cu-based materials are sum-marised in Fig 28a and b Most of the alloys shownfail via MVC and the pressure induced ductilityresponse is nominally linear with an increase inpressure A change in fracture mechanism from press-ure sensitive MVC fracture to pressure insensitiveductile rupture was observed149 in Cu-30ZnCu-40Zn Cu-67Ge and Cu-9middot7Ge materials atintermediate levels of superimposed pressure consist-ent with the change in slope of the fracture strain vsuperimposed hydrostatic pressure summary pro-vided in Fig 28a However the most dramatic effectsof pressure were obtained on brittle Cu-002Bi mater-ials which failed via low ductility intergranular frac-ture at low or atmospheric pressure with a transitionto high ductility ductile fracture at modest levels ofpressure and a complete suppression of intergranularfracture152 as shown in Fig 26a and b

1200

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bullbullbull bull

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200 400 600 800 1000 1200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

60

50c 40

00~ 30ll~~ 20~

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60

d 5000 40~ll 30~~~S 200Z 10-

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from atmospheric pressure to relatively modest levelsof pressure103 Pressures of sufficient magnitude havebeen shown to completely suppress damage associa-ted with inclusions in 6061AI (Ref 103) as well asAI-1Si-07Mg-04Mn alloys123 Consistent with thediscussion above the fracture strain of these alloyswas highly pressure sensitive at low levels of superim-

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

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--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

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-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

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00

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(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

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--~- Zn-AIIRuhhlrskeCII~

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-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

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bull 6061 AI-OA 103

bull (X- brass 86

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----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

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Page 23: Effects of Hydro Static Pressure on Mechanical

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 167

1200

(a)

(b)

1000800600

400200

_ 0 2124AI-lTA ]5~201

----II 2] 24AI-OA 152201

-S MB85_UA18919o195

-m t1B85-0l 189190195

-0 6061AJ-lJA 18919(1195

G 6061 AI-OA 189 I YO J 95

s - 7075AI-T4 99

--k - 7075AI-T65 1(TR) 5051

l- - 7075AI-T651(WR) 5051

bull - 7075AI-T651(RW) 5051

bull Al 149

-ltgt--- Al-l Si-O7Mg-OAMn 123

--[ 20 14Al-rr6 J 52201

- - - -+- - - - A356AI-T6] S4

o

40

60

50

=C 40~~~ 30rBtJcr 20~

00

60

~

~~~~~f~~~~~~L~- tmiddot -I Ttl 1o 200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

E 20roZ

= 50er

00

2000

(a)

(b)

middot bull Pure Fe I I g

middot bull Pure Fe 149

middot bull Impure Fe 149

Cast Iron Typell 123

middotYmiddotmiddotmiddotmiddot Cast Iron Typell 123

-D PM Tunsten 74

-D Plvt Tungsten 72

middot [9 Arc-melted Tungsten 72

middot middot8 Arc-melted Tungsten 7 I

-0- Cll-O02Bi J 52

~ Magnesium 74

~J--- Zinc J 21

--02middot-- Zinc 1[2

~ZI1-AI ~()skc() J2~

--~- Zn-AIIRuhhlrskeCII~

-D - Amorphous Pd-Cu-Si 323

(Compression)

-vmiddotmiddot -Amolvl1OuS Pd-Cu-Si 323

--0 - Amorphous Zr-Ti-Ni-Cu-c

o 500 1000 1500 2000Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

Effect of pressure on fracture strain of somebcc metals amorphous metals and otherbrittle metals

160

140 ~5 I

eo 120 ir~~ 100rB

80 8~eor~ 60 Jx

E Cd middot5r 40 Ii i~ xX ~ ill

26

Superimposed Hydrostatic Pressure MPa

Figures 31 and 32 summarise very recentwork obtained on various aluminium alloy com-posites as well as magnesium alloy compos-ites152184189-191194-197200201343382Although thefracture strainductility of such materials are typicallyvery low at atmospheric pressure because of the highvolume fraction of hard non-deforming reinforce-ment the fractography of such materials has revealedthat fracture occurs via a MVC type phenom-

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

27 Effect of pressure on fracture strain ofaluminium and aluminum alloys

enon189-201383-390Void nucleation in such materialsis associated with the brittle reinforcement particleswhile ductile fracture in the matrix (ie aluminiumalloy magnesium alloy) is typical The pressure

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

bull

o 6061AI-UA 103

bull 6061 AI-OA 103

bull (X- brass 86

bull

bullo

bull300

20

~middotc 150gt~0

I 10~~ bull 0eel-t bull~ bullee 05Q)bull~

00a 100 200

CLI GS2011m] 1j8

-0-- Cu GS70~lm IV)

ERCll Cll 121

----T---- Cu-15Zn GS=811m 149

--- bull---- Cu-30Zn GS=2011m 149

- - - -1- - - - Cu-40Zn GS=2511m 149

----1---- Cu-299Zn GS=7011m 87

-- Cu-67Gc GS3111Tn J 49

- -- - - Cu-97Ge GS=30~lm I J 49

Cu-45Ge GS=23~lm l4e)

----S- Cu-396Zn-29Pb 85

60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

(a)

(b)

1000

1000

800

800

600

600

400

400

200

200Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

00

a

60I 50l-t

~Q) 40l-ts~ee 30bull~S 20bull0Z 10

00a

induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

~OJ) Cj 15 ce

en~ 10 lt~~ 10gt ~lt QI)

05 ~- ---0 -- VA - OA 05 ~~gt(b) lt00 00

0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

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600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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338 A H COTTRELL Theory of crystal dislocations 1964 NewYork Gordon and Breach

339 T E DAVIDSON J C UY and A P LEE Trans AIME 1965233820

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in 1994 World PM congress (ed C Lall et al) 269 1994Princeton NJ MPIF

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345 P F THOMASON Ductile fracture of metals 1990 New YorkPergamon Press

346 J F KNOTT Fundamentals of fracture mechanics 1973London Butterworths

347 A W THOMPSON and J F KNOTT Metall Trans A 199324A523

348 R O RITCHIE and A W THOMPSON Metall Trans A 198516A233

349 F A McCLINTOCK and A S ARGON Mechanical behaviour ofmaterials 1966 Reading MA Addison-Wesley

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Strength of metals and alloys - ICSMA 7 Montreal Aug1985 1193 1985 New York Pergamon Press

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356 A N STROH Adv Phys 1957 6418357 A N STROH Phios Mag 1958 3 597358 1 FREIDEL Dislocations 1964 New York Pergamon Press359 1 F KNOTT and A H COTTRELL J Iron Steel Inst 1963

201249360 J F K~OTT J Iron Steel Inst 1966 204 104361 1 F KOTT J Iron Steel lISt 1966 204 1014362 J F K~OTT J Iron Steel Inst 1967 205 288363 OROWAN Trans Inst Eng Shipbuilders Scotland 194589 1165364 N N DAVIDENKOV Dinamicheskaya ispytania metallov 1936

Moscow USSR365 1 1 LEWANDOWSKI and A W THOMPSON Metall Trans 1986

17A 1769366 J J LEWANDOWSKI and A W THOMPSON Acta Metall 1987

35 1453367 A SAMANT and 1 J LEWANDOWSKI Metall Mater Trans A

1997 28A 389368 D TEIRLINCK F ZOK J D EMBURY and M F ASHBY Acta

Metall 1988 36 1213369 D TEIRLINCK M F ASHBY and J D EMBURY in Advances in

fracture research - ICF 6 New Delhi India Dec 1984 105New York Pergamon Press

370 w M GARRISON Jr and N R MOODY J Phys Chem Solids1987 48 1035

371 A W THOMPSON Metall Trans A 1987 18A 1877372 L M BROWN and J D EMBURY in Proc 3rd Int Conf on

Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

374 s H GOOD and L M BROWN Acta Metall 197927 1375 L M BROWN and w M STOBBS Phios Mag 197634 351376 P F THOMASON Ductile fracture of metals 94 1990 New

York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

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MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

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405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

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411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

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413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

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Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

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Rev 1993 38 193

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168 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600500400

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60Superimposed Hydrostatic Pressure MPa

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

28 Effect of pressure on fracture strain of copperand copper alloys

29 Area fraction of voids in 6061AI-UAOA(Ref 103) and a-brass86 as function of super-imposed hydrostatic pressure

slight increase in the ductility obtained in compositeswhich failed via intense shear between the reinforce-ment and globally (eg 2124-SiCw MB-78-15SiCp_UA)152192194201as shown in Fig 31aInterestingly the AI-AI3 Ni composites152201shownin Fig 31a initially exhibited pressure induced duc-tility increases until the fracture mode changed fromdimpled fracture (ie MVC) to intense localised shearThe intervention of the intense localised shear fracturemode which was promoted by the pressure inducedsuppression of damage in the composite resulted inan eventual pressure independence of the ductility onfurther increases in pressure as shown in Fig31aand b

Effects of changes in reinforcement volume fractionand size on the pressure response have been recordedfor both aluminium alloy and magnesium alloymatrixes though detailed investigations of thecause(s) of such observations are currently lacking The effects of changes in microstructural featuresheattreatment on the evolution of different types ofdamage (eg reinforcement cracking interface failurematrix voiding) at atmospheric pressure have beenstudied in a few cases for such composites197199though relatively little complementary work hasbeen done for materials tested with superimposedpressure199

1200

1200

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(b)

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1000

800

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induced ductility response is often extraordinary inthese materials with ductility levels approaching (andexceeding in some cases eg Refs 189 190 200) thatof the matrix materials depending on the heat treat-ment utilised At sufficiently high levels of superim-posed pressure for both particulate and long fibresystems the suppression of void growth occurs tosuch an extent that matrix flow into reinforcementnucleated cavities occurs184187189-191196197201391

Clear differences in the pressure response areobtained for different alloys and heat treatmentswhile there are also effects of reinforcement type(eg whisker v particulate) reinforcement size andreinforcement volume fraction on the levels of press-ure induced ductility obtained As observed with someof the monolithic aluminium alloys there was only a

International Materials Reviews 1998 Vol 43 NO4

Effects of pressure on fracture stressThe general effects of superimposed pressure on thetrue fracture stress for a variety of steels fromBridgmans work36 are shown in Figs 33-37 Whileit has typically been observed that the fracture stressincreases in a linear manner with an increase insuperimposed pressure the slope of such increaseswere not consistent between the various materialstested in Bridgmans early works In particular a fewof the materials investigated in Figs 33-37 exhibitednon-linear changes in the pressure induced fracturestress change with initial increases in the fracturestress followed by a plateau or decrease in the frac-ture stress at higher levels of superimposed pressureIn these cases a macroscopic change in fracture mech-anism was observed (eg ductile fracture transition toductile rupture or localised shear)

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 169

TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

en~8 -fr-- UA-A-- OA - 35 middot0=1- 25 gt~ 30 ~

0N

00 20(_ 25 ~~ ~middot0 ~gt 15 20 ~~~ j

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en~ 10 lt~~ 10gt ~lt QI)

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0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

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400

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~- --

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AZ91-20SiCp521Un-T6193

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020

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a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

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o

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31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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TensileAxis

a P=Ol MPa P=150 MPa P=300 MPa30 40

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0 50 100 150 200 250 300 350Superimposed Hydrostatic Pressure MPa

30 a Appearance of voids adjacent to fracture surface of 6061AI tensile specimens fractured at pressuresshown103 and b average void size and average void aspect ratio in 6061AI-UAOA as function ofsuperimposed hydrostatic pressure 103

More recent works conducted on brittle and semi-brittle materials including intermetallics152154-166168-170composites52185-187193195189-201and amorph-ous metals323324 have revealed quite different effectsof superimposed pressure on the fracture stress Thepressure induced change in the fracture stress of avariety of brittle and semibrittle metals includingsome intermetallics and amorphous metals323324 aresummarised in Figs 38a and b 39a and b and 40aand b The data summarised in Figs 38a and band 39a and b reveal that significant increases inthe fracture stress often accompany an increase inpressure while Fig40a reveals similar behaviour forpolycrystalline Ni3AI (Ref 170) and NiAI that wascast and extruded155-163 In some of these cases themagnitude of the pressure induced increase in thefracture stress was roughly equivalent to the level ofpressure applied in accord with equation (9) Aspresented above this is consistent with a propagationcontrolled brittle fracture criterion which requiresachieving a maximum principal stress Extensivemetallographic and fractographic investigationsrevealed that such increases in fracture stress weredue to the pressure induced suppression of damage(ie intergranular fracture cleavage fracture) In thecase of cast and extruded NiAl it was demonstratedthat the ductility fracture stress and percentage ofintergranular and cleavage fracture present on thefracture surface was affected by level of superimposedhydrostatic pressure163 Increased levels of pressureproduced increases in the level of intergranular

fracture and changed the remaining fracture fromtransgranular cleavage to quasicleavage The obser-vations of arrested microcracks in Ni3 AI and castand extruded NiAI specimens tested with high press-ure is strongly supportive of such a fracture criterionas reviewed by others155-157161163170

In contrast to this behaviour some of the metalssummarised in Figs 38a and band 39a and b exhibitthat somewhat lower increases in fracture stressaccompany an increase in pressure Figures 38a and band 40a and b also illustrate that recrystallised Moamorphous metals323324 and single crystal NiAI aswell as higher strength variants of polycrystallineNiAI exhibit pressure independent values for thefracture stress when testing is conducted with super-imposed pressure or after simple pressurisation132163The broken lines in Figs 38b 39b and 40b representa slope of 1 in the change in fracture stress v pressureThe pressurisation treatments on cast and extrudedNiAl produced significant reductions in the yieldstress as shown above in Fig 7a-c via the generationof mobile dislocations However neither the fracturemode nor the ductility andor fracture stress weresignificantly affected by simple pressurisation to levelsof pressure well in excess of the yield stress of themateriaI155157161163The lack of pressure dependenceof the fracture stress of single crystal NiAI whichis similar to that reported for MgO (Refs 180 181)and a variety of other brittle systems suggests thatfracture may be nucleation controlled in such casesat least up to the pressures utilised Fracture in the

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

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170 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

600

(a)

500

bull

EB

400

EB

~- --

bull300200

AZ91-19SiCp 15Ilm-T6 193

AZ91-20SiCp521Un-T6193

-

bull-_--

-- bull100 200 300 400 500 600

EB EB

(b)

100

EE

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

020

= 015l-I

(jjC1i 010l-Isu~l-I~

005

000

0

100

= 80l-I

(jjC1i 60l-Isu~l-I 40~8l-I0 20Z

000

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

32 Effect of pressure on fracture strain ofdiscontinuously reinforced magnesium matrixcomposites 193

amorphous metals323324 appears to occur via intenselocalised shear which is not highly pressure sensitiveat least at the pressure utilised Testing at higherpressures would be useful to explore in order todetermine if pressures of sufficient magnitude couldinduce significant ductility or fracture stress increasesin single crystal NiAI and amorphous metals

The composites data summarised in Fig 41a gener-ally reveal a linear increase in the fracture stress withan increase in pressure However the magnitude ofthe increase in fracture stress does not always scalelinearly with the increase in pressure as shown inboth Fig 41a and b and by the broken line of slopeequal to one in Fig 41b As with Bridgmans data inFigs 33-37 there was often a change in macroscopicfracture mode from dimpled fracture (ie MVC) tointense shear at sufficiently high levels of pressure

1000

(a)

(b)

200 400 600 800 1000Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

o

bull

A 6090Al-25SiCp-T6 193

---If--- f09() j 2-SC S 19~~o I - ) lp- I

--__SJ- _-- 1B78-15SiCp 13~lrn -UA 194

I] 1 l-B-7 8 IS co- -Il () 194lY lt _ ~ 1 P pn1 - 1

0 --A356-10SiCp 126pm-T6 84

- bull -- A356-20SiCp 126tm -T6 184

)( AI-AI Ni 1523

-v-- 6061Al-15AlO 13Jlm-OA 195197( 3

-6- MB85-15SiCp 13Ilm-UA 194

-A- - MB85-15SiCp 13Ilm-OA 194

-0 -- 2014AI-20SiCp 13Jlm-AE 152

-e--- 2014Al-20SiCp13Ilm-T6152

----0 middot 2124AI-14SiCw IJlm-UA 152201

_ - 2124AI-14SiCw 1Ilm-OA 152201

- _ - 1Qi 197--fs-- 6061 Al-15Al 0 13j1111 -UA _

- ~

30

25

= 20l-I

00C1i 15l-I

3u~

10l-I~

600

= 500l-I

00 400C1il-I

3300u~

l-I~e 200 bull 0l-I --0Z 100

(5

a fracture strain v superimposed hydrostatic pressureb normalised fracture strain v superimposed hydrostatic pressure

31 Effect of pressure on fracture strain ofdiscontinuously reinforced aluminium matrixcomposites

Effects of pressure on fracture toughnessWhile it is clear that an extensive variety of materialshave been tested in uniaxial tension with superim-posed pressure very little work has been conductedin order to determine the effects of such conditions

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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1997 28A 2297354 J1 LEWANDOWSKI and J F KNOTT in Proc 7th Int Conf on

Strength of metals and alloys - ICSMA 7 Montreal Aug1985 1193 1985 New York Pergamon Press

355 J R LOW in Relation of properties to microstructure 1631953 Novelty OH ASM

356 A N STROH Adv Phys 1957 6418357 A N STROH Phios Mag 1958 3 597358 1 FREIDEL Dislocations 1964 New York Pergamon Press359 1 F KNOTT and A H COTTRELL J Iron Steel Inst 1963

201249360 J F K~OTT J Iron Steel Inst 1966 204 104361 1 F KOTT J Iron Steel lISt 1966 204 1014362 J F K~OTT J Iron Steel Inst 1967 205 288363 OROWAN Trans Inst Eng Shipbuilders Scotland 194589 1165364 N N DAVIDENKOV Dinamicheskaya ispytania metallov 1936

Moscow USSR365 1 1 LEWANDOWSKI and A W THOMPSON Metall Trans 1986

17A 1769366 J J LEWANDOWSKI and A W THOMPSON Acta Metall 1987

35 1453367 A SAMANT and 1 J LEWANDOWSKI Metall Mater Trans A

1997 28A 389368 D TEIRLINCK F ZOK J D EMBURY and M F ASHBY Acta

Metall 1988 36 1213369 D TEIRLINCK M F ASHBY and J D EMBURY in Advances in

fracture research - ICF 6 New Delhi India Dec 1984 105New York Pergamon Press

370 w M GARRISON Jr and N R MOODY J Phys Chem Solids1987 48 1035

371 A W THOMPSON Metall Trans A 1987 18A 1877372 L M BROWN and J D EMBURY in Proc 3rd Int Conf on

Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

374 s H GOOD and L M BROWN Acta Metall 197927 1375 L M BROWN and w M STOBBS Phios Mag 197634 351376 P F THOMASON Ductile fracture of metals 94 1990 New

York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

International Materials Reviews 1998 Vol 43 No4

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 171

Superimposed Hydrostatic Pressure MPa

i 1bull

0l

Ii Iii I I I i

Fe-OS5C-O 35Nl n-O04P-O04S-0 20Si-3 45Ni- 23Cr(aI)-received)Fe-O3C-O18Mn-OO I ] P-O02S-O07Si-298N i- 1 ] SCr(al)-received)Fe-O26C-023Mn-002P -0025S-O06Si-304Ni-I4Cr(as-received)Fe-O3C -O241vln-O024P-O()31 S-O08Si-296Ni-J29Cr(as-received)1045 Steel (as-received)Fe-O6C-O7rv1n-003P-O03S-I9Si(as-received)oil-quenched

r- r

ltgt-

--0

_----6--

---

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

3000

lj

II ~

I I

250020001500

bull bull

1000

-- annealed fine-grainedannealed coarse-grainedbrine-quenchedspheroidisedbrine-quenchedtelnpercd 315degCbrine-quenchedtempered 315degCbrine-quenchedtenlpered 480degC

i Iii Ii iii i i

500

I I

__--fSJ--- Fe-O34C-O75tvln-O017P-O033S-O18Si (as-received)

-0 - Fe-045C-O83Mn-O016P-O035S-O19Si (as-received)nonnalised 900degC-0

----0

---6-

- ------+---11---

5000

6000

33 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

35 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

34 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

on the fracture toughness Such information could beof practical importance to a variety of applicationswhere such materials might be used in pressurisedenvironments while the information generated couldalso be useful in the evaluation or generation ofmodels for fracture toughness Part of the reason forthe lack of such published data relates to the difficultyin conducting such experiments at high pressure inaddition to the limitations placed on specimen sizes

Figures 42a and band 43 illustrate the experimen-tally obtained data for fracture toughness at differentlevels of hydrostatic pressure for different orientationsof 7075AI- T651 (Refs 50 51) as well as for sphe-roidised graphite cast iron83 respectively In theformer case significant increases in the toughnesswere obtained with an increase in pressure as shownin Fig 42a while the ratio of the toughness obtainedat high pressure to the value obtained at atmosphericpressure is presented in Fig42b as the normalisedfracture toughness The toughness increases in thiscase were attributed5051 as due to the suppression ofMVC fracture Void nucleation at particles ahead ofthe crack tip within the 7075AI alloy was suppressedand was consistent with the increase in crack openingdisplacement (COD) shown in Fig 44 that accom-panied the pressure induced increase in toughnessThe toughness data in this case were compared tovarious models (eg Refs 392 393) of fracturetoughness for materials failing via MVC and the data

International Materials Reviews 1998 Vol 43 NO4

o

bull ~

Fe-O68C-O71 Nln-OO 13P-O02SS-O19Si (as-received)Fe-09 -04 7Mn-OO15P-0036S-011 Si (as-received)normal ised 900degCannealed fine-grainedannealed coarse-grained

-- bline-quenchedspheroidisedbrine-quenchedtempered 315degCbrine-quenchedtempered 480degC

-0

middot--0---0

--6-- ------ --+-

1000

6000

Cl3~ WOOC~

oo 500 1000 1500 2000 2500 3000

Superimposed Hydrostatic Pressure MPa

C 5000~~rpound 4000rrCl

ui 3000

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

International Materials Reviews 1998 Vol 43 NO4

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

374 s H GOOD and L M BROWN Acta Metall 197927 1375 L M BROWN and w M STOBBS Phios Mag 197634 351376 P F THOMASON Ductile fracture of metals 94 1990 New

York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

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172 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

bullbull~~~ Dttmiddot 0

11- middot_middot bull

6000

~E 2000-i~~ 1000

~ 5000~~~4000V)V)~

00 3000

II Fe-O094C-O361tlN-O(23P-O022S-O35Si-1226Cr-046Ni-OSIvlo(as-received)

-8- Fe-O067C-O05MN-O02P-O03S-051 Si-17 49Cr-041Ni(as-received)

- -A- FemiddotmiddotO058C-O7ol1N-O03P-OOJ3S-O85Si-1851 Cr-895Ni-O2Cu(as-received)

- bull - Fe-O051 C-O59MN-O03P-002S-04 7Si-1831 Cr-l O27Ni-02Cu(as-recei ved)

--0 High-carbon Steels48HRC

-0--- 51HRC-- -8---- 56HRC----0 60HRC----1-- 63HRC

ClfJ

[] cr

500 1000 1500 2000 2500 3000Superimposed Hydrostatic Pressure MPa

oo

6000

~ 5000~~

~ 4000V)V)~(j 3000~ -

e 2000~~ 1000

rsJ 1045 Steel (as-received)C) water-quenched from 860degC] water-quenched from 860degC

403HRC ltgt quenched into salt 0) 425degC

917HRB

-D- - quenched into salt 0) 595degC855HRB

v -vater-quenched frorn 860degC 21 HRC- teJnpered pearlite 258HRC

_ middotR - tcrnpercd lnartcnsite 283HRC

36 Effect of pressure on fracture strain of varioussteels tested by Bridgman36 o

o 500 1000 1500 2000 2500 3000

were found to agree well with such models In con-trast the work on spheroidised cast iron summarisedin Fig 43 as well as similar work on single crystalNiAl (Ref 158) failed to reveal any effect of superim-posed pressure on the toughness again suggestingthat fracture in such brittle materials may benucleation controlled at least up to the pressurestested Additional tests on such materials over a widerrange of pressures might be useful to determine if atransition pressure exists where significant toughnessincreases may be observed

Effects of hydrostatic pressure ondeformation processingGeneral aspects of stress state effects onprocessingThe general deform ability of a material is related toa number of factors including the strain rate stressstate temperature and the flow characteristics of thematerial which are affected by the crystal structureand the microstructure As illustrated in the precedingreview sections changes in the stress state via thesuperimposition of hydrostatic pressure can clearlyexert a dominant effect on the ability of a material toflow plastically regardless of the other variablesIn many forming operations controlling the meannormal stress Urn is critical for success394395 Com-pressive forces which produce low values for Orn

increase the ductility as illustrated above for a varietyof structural materials while tensile forces which

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

37 Effect of pressure on fracture strain of varioussteels tested by Bridgman36

generate high values for Orn significantly reduce theductility and often promote a ductile to brittle trans-ition Thus metal forming processes which impartlow values for Orn are more likely to promote deforma-tion of the material without significant damage evol-ution394395 There are a variety of industriallyimportant forming processes which utilise the ben-eficial aspects of a negative mean stress on the form-ability such as extrusion wire drawing rolling orforging In such cases the negative mean stress canbe treated as a hydrostatic pressure that is impartedby the details of the process 394395 More direct utilis-ation of hydrostatic pressure includes the densificationof porous powder metallurgy products where bothcold isostatic pressing (CIP) and hot isostatic pressing(HIP) are utilised In addition many superplasticforming operations conducted at intermediate to highhomologous temperatures utilise a backpressure ofthe order of the flow stress of the material in orderto inhibiteliminate void formation68105150 Pressureinduced void inhibition in this case increases theability to form superplastically in addition to posi-tively impacting the properties of the superplasticallyformed material

While it is clear that triaxial stresses are present inmany industrially relevant forming operations themean stress may not be sufficiently low to avoid

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 173

I(a)

bullo

c

bull

I I i

EE

o

bull~

(b) jI I i i

600 800 1000 1200

bullEEo

400

In Oot Be -L)c

AZ91 101

AZ91 193

0

PlvI Be 45

Cast and rolled Be 54~m 55

Cast and rolled Be 68~n1 55

Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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Cast and rolled Be 150~m 55

EI 1middot Z ]71ectro yUc 11 _

200

Ii

o

o[S]

EB

200 400 600 800 1000 1200 1400 1600Superimposed Hydrostatic Pressure lVlPa

o

oo

~ 1200~~~1000

[I

[I~(i 800Qj

~ 600~~S 400

1200 rL

1000~~E 800 r~ ~~ 600 r~ t 8J

~ 400 ~ ~~ ~ 200 Go

Q)

~ 200 ( 6a ()~~ ~ bull ~ ~U 0 wmiddot~~ 16 i Ii

~

(b)

200 400 600 800 1000 1200

Cast Fe 123

12Cast rvlo

I ~1

Rccrystalliscd CastIvl0 laquof ] 80 K ~71PM Tungsten

71Arc-Melted Tungsten

bull

i I i I iii iii i j iii i I Iii i I

-200 0

bull

Superimposed Hydrostatic Pressure MPa

Superimposed Hydrostatic Pressure MPa

1200

1200 FQ r~ 1000pound 800

~

rrcJ(i 600

cJ ~s 400

f~C

~ 200- 0

cJ t-eJ)

S -2000 -400

-400

-1000 L g () 6L ~-_(Jc - Q ~I bull L t ~800 ~ 0deg 6 bull~ f- 0 0

r f li fj~ 600

bullbullbull (jbull bullCol bull bull bullB 400 bull bull bulllI bull- bull~ 200 t bull

a I I I r I J

a 200 400 600 800 1000 1200

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

38 Effect of pressure on fracture stress of bccmetals

Superimposed Hydrostatic Pressure MPa

damage in the form of cracks Although a generaldiscussion of each forming process is beyond thescope of this review a few general key points areprovided below while it is clear that (Jm can belowered further by superimposing a hydrostatic press-ure Recent articles and books highlighting such tech-niques are provided186288289304391394-413

Some of the key findings and illustrations aresummarised in order to highlight the importance andeffects of hydrostatic pressure whether it arises dueto the die geometry or is superimposed via a fluidon the formability Various textbooks394395 and art-ic1es414415 have reviewed the factors controlling theevolution of hydrostatic stresses during various form-ing operations In strip drawing the hydrostatic press-ure (P = - (J 2) varies in the deformation zone andis affected by both the reduction r as well as theextrusion die angle rx as illustrated in Figs 45 and 46Both figures illustrate that the mean stress (rep-resented by (J 2) may become tensile (shown as negative

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

39 Effect of pressure on fracture stress of hcpmetals

values in Figs 45 and 46) near the centreline of thestrip Furthermore both the distribution and magni-tude of hydrostatic stresses are controlled by ex and rwith the level of hydrostatic tension at the centrelinevarying with ex and r in the manner illustrated inFig 46 Consistent with the previous discussions onthe effects of hydrostatic pressure on damage it isclear that processing under conditions which promotethe evolution of tensile hydrostatic stresses will pro-mote internal damage formation in the product inthe form of microscopic porosity near the centrelineIn extreme cases this can take the form of inter-nal cracks Significant decreases in density (due toporosity formation) after slab drawing have been

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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345 P F THOMASON Ductile fracture of metals 1990 New YorkPergamon Press

346 J F KNOTT Fundamentals of fracture mechanics 1973London Butterworths

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348 R O RITCHIE and A W THOMPSON Metall Trans A 198516A233

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Moscow USSR365 1 1 LEWANDOWSKI and A W THOMPSON Metall Trans 1986

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fracture research - ICF 6 New Delhi India Dec 1984 105New York Pergamon Press

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Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

374 s H GOOD and L M BROWN Acta Metall 197927 1375 L M BROWN and w M STOBBS Phios Mag 197634 351376 P F THOMASON Ductile fracture of metals 94 1990 New

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29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

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403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

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406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

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408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

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411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

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Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

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Rev 1993 38 193

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174 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

2014AI-20SiCp 13Jlm- T6 152

~ 1) 8 5 1 - S (~ ) lmiddot 195tV ) ~ middot-i5 bull1 pl)~unJ-UAIvlB85-] 5SiCp 13lm -OA 195

AZ91- 19S iCp 15Jlrn _T6 193

AZ91-20SiCp52IJ-In-T6193

EB

Superimposed Hydrostatic Pressure MPa

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

Effect of pressure on fracture stress ofdiscontinuously reinforced metal matrixcomposites

1000

~ 800~~ 0

rJ EBrJJ 600 Q)1gtlo- 6

00 ~ EB bullEB 6 bull

Q) 400 EB bull bulllo- 1gtE~ bull~l-lt~ 200

(a)0-400 -200 0 200 400 600

Superimposed Hydrostatic Pressure MPa

~ 600~~riJ 400rJJCl)l-lt

00Q) 200 0lo- at 6EB6E

6 bull~ bull~ EBl-lt 0~

EB5~ -200=~

(b)-=u -400-400 -200 0 200 400 600

411500

EB

1000

===~lSI

500

iJ -v

oSuperimposed Hydrostatic Pressure MPa

o 500 1000 1500Superimposed Hydrostatic Pressure MPa

o

~ 2000~rJ~ 1500lo-

00~ 1000E~~lo-

~ 500

(a)2500

-0--- NiAl Single Crystal 163

-0-- NiAl PM 163

--tr-- NiAI CastExtruded 163

--0- NiAl CastlExtruded

Pre-pressurized 156

-0- --CP-NiAI 166

-ISI- - - HP-NiAI 166

-EB- - - NiAI-N 166

---e---- Ni AI 1521703

-iJ - Amorphous Pd-Cu-Si 23

(Compression)- -T - - Amorphous Pd Cu-Si 123

Amorphous Zr-Ti-Ni-Cu-Bl 32middot1

1500~ (b)~~1000lo-

00

Q)I()=~

-=U -500 -500

a fracture stress v superimposed hydrostatic pressureb normalised fracture stress v superimposed hydrostatic pressure

40 Effect of pressure on fracture stress of NiAINi3AI and amorphous metals

recorded414415particularly in material taken fromnear the centreline generally consistent with the levelsof tensile hydrostatic pressure present as predictedin Figs 45 and 46 Furthermore it was foundthat greater losses in density occurred with smallerreductions (ie small r) and higher die angles (ielarger a) consistent with Fig 45 Such damage willclearly reduce the mechanical and physical propertiesof the product Consistent with the previous dis-cussion it has been found that the loss in density ina 6061-T6 aluminium alloy could be minimised orprevented by drawing with a superimposed hydro-static pressure as shown in Fig 47 (Ref 415) In somecases increases in the strip density were recordedapparently due to elimination of porosity which waseither present or evolved in previous processing steps

International Materials Reviews 1998 Vol 43 No4

It is clear that maintaining a compressive mean stresswill increase the formability regardless of the formingoperation under consideration Materials with limitedductility and formability can be extruded as demon-strated below for a variety of composites184186401and the intermetallic NiAI (Refs 154 162 164) ifboth the billet and die exit regions are under highhydrostatic pressure In the absence of such a ben-eficial stress state Figs 45 and 46 illustrate that largetensile hydrostatic stresses can evolve in formingoperations which are conducted under nominallycompressive conditions Thus it should be noted thatthe example of strip drawing provided above is alsorelevant to other forming operations such as extrusionand rolling where similar effects have been observedalong the centreline of the former and along the edgesof rolled strips in the latter During forging andupsetting barrelling due to frictional effects causestensile hoop stresses to evolve at the free surface andcan promote fracture in these locations33934o394395

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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62 S B BINER and W A SPITZIG in Modeling of the deformationof crystalline solids (ed T C Lowe et al) 545 1991Warrendale PA TMS

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356 A N STROH Adv Phys 1957 6418357 A N STROH Phios Mag 1958 3 597358 1 FREIDEL Dislocations 1964 New York Pergamon Press359 1 F KNOTT and A H COTTRELL J Iron Steel Inst 1963

201249360 J F K~OTT J Iron Steel Inst 1966 204 104361 1 F KOTT J Iron Steel lISt 1966 204 1014362 J F K~OTT J Iron Steel Inst 1967 205 288363 OROWAN Trans Inst Eng Shipbuilders Scotland 194589 1165364 N N DAVIDENKOV Dinamicheskaya ispytania metallov 1936

Moscow USSR365 1 1 LEWANDOWSKI and A W THOMPSON Metall Trans 1986

17A 1769366 J J LEWANDOWSKI and A W THOMPSON Acta Metall 1987

35 1453367 A SAMANT and 1 J LEWANDOWSKI Metall Mater Trans A

1997 28A 389368 D TEIRLINCK F ZOK J D EMBURY and M F ASHBY Acta

Metall 1988 36 1213369 D TEIRLINCK M F ASHBY and J D EMBURY in Advances in

fracture research - ICF 6 New Delhi India Dec 1984 105New York Pergamon Press

370 w M GARRISON Jr and N R MOODY J Phys Chem Solids1987 48 1035

371 A W THOMPSON Metall Trans A 1987 18A 1877372 L M BROWN and J D EMBURY in Proc 3rd Int Conf on

Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

374 s H GOOD and L M BROWN Acta Metall 197927 1375 L M BROWN and w M STOBBS Phios Mag 197634 351376 P F THOMASON Ductile fracture of metals 94 1990 New

York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 175

43 Effect of pressure on fracture toughness ofspherodised graphite cast iron83

minimising the amount of damage imparted to thebillet material Such processing is used in the pro-duction of wire while the concepts covered below aregenerally applicable to the various forming operationsoutlined above and specifically those dealing withextrusion

100 200 300 400 500 600 700 800Superimposed Hydrostatic Pressure MPa

oo

100N

-8~ 80~

~~ 60rJJC)Ccell 400~C) l-o

E 20 bulleJ ~l-o~

-+

7075AI- T651 51

-6-- IR 3PB- -A- - rIR CT

- - -0- - - TW 3PB

- -e- - TW CT

---- J--- VR [3PB

- -11- - WR eT

-- -0- -- RV 3PB

- - -~- RV leT

7075AI-T6515o

----r--- TR 3PB 1-0- TW3PB------Q----- VR 3 PB

----------~-)_------- R V 3 P B

100N [_

-E t~ 80

-0~

Superimposed Hydrostatic Pressure lVIPa

I

(a) lo =CS J - I I ~ I 1 I 1 1 I I I 1 J

o 100 200 300 400 500 600 700 800

0050

Hydrostatic extrusion fundamentalsHydrostatic extrusion is a method of extruding abillet through a die using fluid pressure insteadof a ram which is used in conventional extrusionFigure 48 compares conventional extrusion withhydrostatic extrusion the main difference being theamount of billetcontainer contact398 The billetcon-tainer interface in conventional extrusion has beenreplaced by a billetfluid interface in hydrostaticextrusion Three main advantages result

1 The extrusion pressure is independent of thelength of the billet because the friction at the billetcontainer interface is eliminated

2 The combined friction of billetcontainer andbilletdie contact reduces to billetdie friction only

3 The pressurised fluid gives lateral support to thebillet and is hydrostatic in nature outside the deforma-tion zone preventing billet buckling Skewed billetshave been successfully extruded under hydrostaticpressure397

800

- ]

fi 605

Eno 40Eo-

JJ 40 ~iIIIIiil I I Ilr -E _1~~I ~~~ ~i~~f~~1~~~-~ (bll

00 f I I I Jo 100 200 300 400 500 600 700

44 Correlation between crack opening dis-placement (COD) and fracture toughness of7075AI- T651 tested at various pressures50

International Materials Reviews 1998 Vol 43 No4

Superimposed Hydrostatic Pressure lVIPa

a fracture toughness v superimposed hydrostatic pressureb fracture toughness v superimposed hydrostatic pressure

42 Effect of pressure on fracture toughness of7075AI- T651 (Refs 50 51)

The remainder of this review focuses on a spe-cific procedure which utilises such an approachto enable deformation processing of materials atlow homologous temperatures hydrostatic extru-sion289-292294-296302-308310416417The beneficial stressstate imparted by such processing conditions en-ables deformation processing to be conducted attemperatures below those where various recoveryprocesses occur (eg recovery recrystallisation) while

88do~

~ TR 3PB

0040 0 1W 3PB

0 WR 3PB rOOL~

deg RW (3PB) deg S00300 ltgt 0

0020 6LP deg 0

0010 cfD2 80 ltgtamp0

00000

0 10 20 30 40 50 60 70Fracture Toughness MPa m 112

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

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fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

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structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

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393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

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397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

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MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

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405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

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409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

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Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

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Rev 1993 38 193

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176 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

6061- T6 aluminium

27 redUClon per pass 25deg semi - angle

Pressure Level ~

o AtmosphericA 5000 psio 10000 pSI

a 20000 PSI

V 100000 pSI

----~~---bull ~

2710 -_--~

II

ClI

EuC)

i270000cQ)o

2695

2705

47 Loss of density by growth of microporosityduring strip drawing and effect of super-imposed hydrostatic pressure on diminishingdensity loss4151 in=254 mm 1000 psi=69 MPa

018 016 014 012 010 008 006 004 002Strip Thickness in

Density value adjusted to fiidifferent siartmg moterlol density

2690 0 Encircled points are extrapolations fromwelghmgs in water

Occasionally stick-slip behaviour is observed dueto periodic lubrication breakdown and recovery inwhich case the run-out pressure fluctuates above andbelow the steady state value Stick-slip causes vari-ation in product diameter and represents instabilityin the process Strong billet materials large extrusionratios and slow extrusion rates facilitate this type ofundesirable behaviour

The work done per unit volume in hydrostaticextrusion is equal to the extrusion pressure Pex(Ref 398) The four parameters which control themagnitude of Pex are die angle reduction of area(extrusion ratio) coefficient of friction and yieldstrength of the billet material

There are three types of work incorporated intoextrusion pressure work of homogeneous deforma-tion or the minimum work needed to change theshape of the billet into final product redundant workbecause of reversed shearing at the deformation zoneand work against friction at the billetdie interface398

As die angle is increased the billetdie interfacedecreases reducing the friction force but the amountof redundant work increases Therefore die angle isa parameter which must be optimised for an efficientprocess as shown in Fig 50a

For a given die angle increased extrusion ratiosyield higher billetdie interfacial areas as sche-matically shown in Fig 50b Consequently higherextrusion ratios require larger extrusion pressures toovercome increased work hardening in the billetregion because of larger strains Higher coefficients of

Numbers representP2k

46 Variation in pressure at centreline for variouscombinations of r and a during strip drawingnote that negative values indicate hydrostatictension414

45 Variation in hydrostatic pressure in deform-ation zone for strip drawing based on fieldshown note that negative values are tensile414

15 20 25 30 35 40Reduction per Pass

There are also disadvantages inherent in hydro-static extrusion The use of repeated high pressuremakes containment vessel design crucial for safeoperation The presence of fluid and high pressureseals complicate loading and fluid compressionreduces the efficiency of the process

A typical ram-displacement curve for hydrostaticextrusion v conventional extrusion is shown inFig 49 The initial part of the curve for hydrostaticextrusion is determined by the fluid compressibilityas it is pressurised A maximum pressure is obtainedat billet breakthrough at which point the billet ishydrodynamically lubricated and friction is lowered(static to kinematic) The pressure drops to an essen-tially constant value called the run-out or extrusionpressure Finally the fluid is depressurised to removethe extruded product Higher pressures are typicallyrequired in conventional extrusion due to increasedfriction between the billet and die as shown398 inFigs 48 and 49

~ OAt~Cl-- 02~- 20deg(l) 0

25degirJJ

25degrJJ -02(l) 30deg~(l) -04SQ) -06joj

$lU -08

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 177

ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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ConventionalExtrusion

HydrostaticExtrusion

bull no billet containerfrictionbull decreased die frictionbull decreased redundantwork

48 Comparison of apparatus for conventional extrusion and hydrostatic extrusion 186187398

middot (16)

analysis is as follows

1pound3 flR In R 1pound2Pex = (J flow dc + e(R _e~ ) (J flow dc

o SIn a ex pound1

where Pex is the extrusion pressure in MPa Rex theextrusion ratio a the extrusion die angle in radiansfl the coefficient of friction (Jflow the flow stress and(J B the yield strength of the billet material in MPa

Avitzurs analysis produced equation (20) with theassumption that the billet material is not work hard-ening The analysis yielded the following results

friction and billet yield strengths will increaseextrusion pressure as well

Mechanical analyses of hydrostatic extrusion havebeen performed by Pugh304 and Avitzur289396 Inboth analyses assumptions are made that the materialdoes not experience deformation parallel to theextrusion axis but undergoes shearing and reverseshearing (fully homogeneous) on entry and exit of thedie Pughs efforts resulted in equation (16) whichassumes a work hardening billet material and acondensed version (equation (19)) which considers anon-work hardening material The result of Pughs

- - - Conventional

Breakthrough --- ----- Hydrostatic

Pressure _ _~ middotmiddot-~1~~ -~ ~~_ - Extrusion

~

Pressure

Iee 9o I ~

~ C

~ ~~ I Vj

Vj i ~ u I

~ i Q

Ram Displacement ~

49 Typical ram-displacement curve for hydro-static extrusion398

where

cl = 0462 [(asin2 a) - cot a]

and

~x ( a )- = 0middot924 -- - cot a(JB sIn2 a

(IIR In R )+ In Rex 1 + ~ ex ex

SIn a(Rex - 1)

Pex 2 ( a )-=~h --2--cota +f(a) In Rex(JB V 3 SIn a

(In Rex)+ fl cot a(ln Rex) 1 + -2-

middot (17)

middot (18)

middot (19)

middot (20)

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

374 s H GOOD and L M BROWN Acta Metall 197927 1375 L M BROWN and w M STOBBS Phios Mag 197634 351376 P F THOMASON Ductile fracture of metals 94 1990 New

York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

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178 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

Before hydrostatic extrusion t after hydrostatic extrusion j mechanicalproperties (tension compression) measured in references listed

Table 4 Summary of hydrostatic extrusion datafor various materials without backpressure

Hardness HV

Material Die angle deg Billet Productt

Iron and steelArmco iron304305 45 76Armco Iron304305 90 76Mild stee1304305 45 113 195-277Steel (Q15C)290-292295308 45AISI 1020 stee398 20 110 285AISI 1020 steel307 90Zn 58304305 45 135 250-320Zn 8304305 45 148 240-2800-2 stee1304305 45 243 3130-2 stee1304305 45 243 370AISI 4340 steel397 45 195 285-301AISI 4340 steel397 45 195 301-393High speed stee1304305 45 260 390-420Rex 448304305 45 340 370High tensile304305 45 374 390-470Cast iron306 45 198 191-249316 stainless steel 20 490

High temperature and refractory metals and alloysBeryll ium290-292295308 45Beryllium398 45Beryllium (hot extrusion)307 90Chromium323 45 174Molybdenum

Rolled304305 45 191 215-263Sinte red304305 45 216 252-298Arc cast305 45 242 263-308

Niobium304305 45 112 176-181Niobium397 20Niobium-2 Zr306 45 281Tantalum304305 45 78-120 127-183Titanium TjAM304305 45 254 262-342Titanium TjAS304305 45 310 299-324Titanium 0_11317 20Ti-6AI-4V317 45 305Tungsten304305 45 440 450-480Vanadium304305 45 270Zirconium304305 45 169 190Zi rco nium304305 30 170Zi rca loy304305 45 292Zircaloy304305 90 265 cont

angle as well as the billet hardness before and afterhydrostatic extrusion are recorded Much of the earlywork utilising such techniques is summarised invarious review papers398402403 which illustratessignificant improvements to the strength-ductilitycombinations possible in materials processed via suchtechniques Early work focused on conventional struc-tural materials such as steels and various aluminiumalloys while highly alloyed and higher strength mater-ials such as maraging steels and Ni-base superalloyswere similarly processed at temperatures as low asroom temperature The beneficial stress state impartedby hydrostatic extrusion enabled large deformationreductions at temperatures well below those possiblewith conventional extrusion where billets often exhib-ited extensive fracturing The benefits of such lowtemperature deformation processing via hydrostaticextrusion included the retention of the coldwarmworked structure as processing was often carried outwell below the recrystallisation temperature of the mat-erial It has often been demonstrated that the prop-

HomogeneousDeformation

Friction Force

Total Extrusion Pressure

OptimumDie Angle

I

I

Die Angle ~

Extrusion Ratio 3

Extrusion Ratio 2

Interfacial Area for

Extrusion Ratio 1

Redundant Work

(a)

(b)

Materials successfully processed viahydrostatic extrusionA variety of materials have been successfully pro-cessed via hydrostatic extrusion as summarised inTable 4289-292294-296302-308310416417 where the die

These equations can be used to predict extrusionpressure for a variety of conditions Predictionof extrusion pressure is both convenient forapparatusbillet design and necessary for safety duringoperation Comparison of these models to some recentexperiments on composites are provided below

50 a Influence of die angle on extrusion pressureand b higher extrusion ratios result in largerbilletdie contact area186398

where Pex is the extrusion pressure in MPa Rex theextrusion ratio ex the extrusion die angle in radiansJ1 the coefficient of friction and (JB the yield strengthof the billet material in MPa The quantity f(ex) isgiven by the following equation

1f(ex) = sin2 ex

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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in 1994 World PM congress (ed C Lall et al) 259 1994Princeton NJ MPIF

342 E J HILINSKI 1 J LEWANDOWSKI T J RODJOM and P T WANG

in 1994 World PM congress (ed C Lall et al) 269 1994Princeton NJ MPIF

343 c LIU and J J LEWANDOWSKI Unpublished research CaseWestern Reserve University Cleveland OH 1991

344 c LIU G MICHAL and J J LEWANDOWSKI in Residual stressesin composites measurement modeling and effects on thermo-mechanical behavior (ed E V Barrera et al) 1993 DenverCO TMS

345 P F THOMASON Ductile fracture of metals 1990 New YorkPergamon Press

346 J F KNOTT Fundamentals of fracture mechanics 1973London Butterworths

347 A W THOMPSON and J F KNOTT Metall Trans A 199324A523

348 R O RITCHIE and A W THOMPSON Metall Trans A 198516A233

349 F A McCLINTOCK and A S ARGON Mechanical behaviour ofmaterials 1966 Reading MA Addison-Wesley

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Strength of metals and alloys - ICSMA 7 Montreal Aug1985 1193 1985 New York Pergamon Press

355 J R LOW in Relation of properties to microstructure 1631953 Novelty OH ASM

356 A N STROH Adv Phys 1957 6418357 A N STROH Phios Mag 1958 3 597358 1 FREIDEL Dislocations 1964 New York Pergamon Press359 1 F KNOTT and A H COTTRELL J Iron Steel Inst 1963

201249360 J F K~OTT J Iron Steel Inst 1966 204 104361 1 F KOTT J Iron Steel lISt 1966 204 1014362 J F K~OTT J Iron Steel Inst 1967 205 288363 OROWAN Trans Inst Eng Shipbuilders Scotland 194589 1165364 N N DAVIDENKOV Dinamicheskaya ispytania metallov 1936

Moscow USSR365 1 1 LEWANDOWSKI and A W THOMPSON Metall Trans 1986

17A 1769366 J J LEWANDOWSKI and A W THOMPSON Acta Metall 1987

35 1453367 A SAMANT and 1 J LEWANDOWSKI Metall Mater Trans A

1997 28A 389368 D TEIRLINCK F ZOK J D EMBURY and M F ASHBY Acta

Metall 1988 36 1213369 D TEIRLINCK M F ASHBY and J D EMBURY in Advances in

fracture research - ICF 6 New Delhi India Dec 1984 105New York Pergamon Press

370 w M GARRISON Jr and N R MOODY J Phys Chem Solids1987 48 1035

371 A W THOMPSON Metall Trans A 1987 18A 1877372 L M BROWN and J D EMBURY in Proc 3rd Int Conf on

Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

374 s H GOOD and L M BROWN Acta Metall 197927 1375 L M BROWN and w M STOBBS Phios Mag 197634 351376 P F THOMASON Ductile fracture of metals 94 1990 New

York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

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Rev 1993 38 193

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 179

Table 4 (cant)

Hardness HV

Material Die angle deg Billet Productt

Magnesium alloysMagnesium304305 45 28Mg-1 AI304305 45 36Mg-1 AI304305 90 36MZTy304305 45 57 76-92ZW3 (cast)304305 45 66 66-85AZ91 (cast)304305 45 93 102-116Mg_Li416417 20AZ91_SiCp416417 20

Aluminum alloys995 AI304305 45 24 43-50995 AI304305 90 24 43-50995 AI39B 20 22 60HE 30 AI (HD44)304305 45 51HE 30 AI (HD44)304305 90 51AI-11 Si304305 45 62 80-93Duralumin 11304305 45 71AFLS304305 45 71 111AD1 (995 AI)290-29229530B 45AD1 (995 A1)290-29229530B 80Alloy A (2-28 Mg)290-29229530B 45Alloy Ak629O-29229530B 451100AI-0398 45AI (annealed)307 90

Copper alloysERCH304305 45 43 120ERCH304305 90 43M2 (997)290-29229530B 45M2 (997)290-29229530B 80Copper (annealed)307 90Copper398 206040 brass304305 45 127 181-1846040 brass (L62)290-29229530B 80

MiscellaneousBismuth304305 45 8 4Yttrium (annealed)39B 90Zinc39B 20NiAI

extruded at 25degC154164t 20 225 725extruded at 300 cC154164t 20 225 370-400

CU_W391

X2080AI-SiCp 186187t 20Bulk metallic glass(extruded at 300degC)417 20

Before hydrostatic extrusion t after hydrostatic extrusion tmechanicalproperties (tension compression) measured in references listed

erties of hydrostatically extruded materials exhibiteda better combination of properties (eg strength duc-tility) than materials given an equivalent reduction viaconventional extrusion186288293299391398399401404-406

The work outlined above on conventional struc-tural materials revealed the potential benefits ofhydrostatic extrusion Many of the original materialsstudied already possessed sufficient ductility to enableprocessing with more conventional deformation pro-cessing techniques while the additional propertyimprovements provided via hydrostatic extrusioncould be achieved by other means However theknowledge gained from such studies on hydrostaticextrusion of conventional materials was utilised inthe optimisation of conventional extrusion die designsand lubricants that could impart such beneficial stressstates in conventional forming processes

The increased emphasis placed on the need forhigher performance materials with higher specific

strength and stiffness in addition to improved hightemperature performance has promoted and renewedresearch and development on a variety of compositesas well as intermetallics These materials typicallypossess lower ductility and fracture toughness thanconventional monolithic structural materials both ofwhich affect the deformation processing character-istics Composite systems may combine metals withother metals or ceramics that have large differencesin flow stress necking strain work hardening charac-teristics ductility and formability In such cases it isimportant to minimise (or heal) any damage whichmight evolve in or near the reinforcement duringprocessing Although intermetallics can be eithersingle phase or multi phase materials the nature ofatomic bonding in such systems may be significantlydifferent to that compared with monolithic metalsresulting in materials with higher stiffness andstrength but reduced ductility formability and tough-ness In such materials it may be particularly import-ant to investigate and understand the effects ofchanges in stress state on the ductility or formabilityIn particular hydrostatic extrusion experiments canprovide important information regarding the pro-cessing conditions required for successful deformationprocessing while additionally enabling evaluation ofthe properties of the extrudate

Hydrostatic extrusion can be conducted viaextrusion into air or extrusion into a receivingpressure The latter process has been shown tohelp to prevent billet fracture on exit from the diefor a range of conventional and advanced struc-tural materials including metals293299398399metalmatrix composites186187288391404-406and intermet-allics154164165311

In composite systems combining metals withdifferent flow strength ductility and necking strainshydrostatic extrusion has been shown to facilitateco-deformation without fracture or instability in sys-tems such as composite conductors288400 and Cu-W(Ref 391) while powdered metals287 have also beenconsolidated using such techniques A limited numberof investigations have been conducted on discontin-uously reinforced compositesl86401 where there ispotential interest in cold extrusion404-406 of suchsystems A potential problem in such systems duringdeformation processing relates to damage of thereinforcement materials as well as fracture of the billetbecause of the limited ductility of the material par-ticularly at room temperature The potential advan-tages of low temperature processing include the abilityto significantly strengthen the composite and inhibitthe formation of any reaction products at the particlematrix interfaces since deformation processing is con-ducted at temperatures lower than that where signifi-cant diffusion recovery or recrystallisation can occurPreliminary work on such systems186401 revealedthat the strength increment obtained after hydrostaticextrusion of the composites was greater than thatobtained in the monolithic matrix processed to thesame reduction In addition hydrostatic extrusioninto a backpressure inhibited billet cracking in anumber of cases187 consistent with similar obser-vations in monolithic metals outlined above398Separate studies187 also revealed an effect of reinforce-

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 183

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in 1994 World PM congress (ed C Lall et al) 269 1994Princeton NJ MPIF

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fracture research - ICF 6 New Delhi India Dec 1984 105New York Pergamon Press

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Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

374 s H GOOD and L M BROWN Acta Metall 197927 1375 L M BROWN and w M STOBBS Phios Mag 197634 351376 P F THOMASON Ductile fracture of metals 94 1990 New

York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

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405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

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409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

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411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

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Page 36: Effects of Hydro Static Pressure on Mechanical

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180 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

ment size on both the hydrostatic pressure requiredfor extrusion (Fig 51a) as well as the amount ofdamage to the reinforcement at various positions in

the extrudate as shown in Fig 51b Table 5 comparesthe experimentally obtained extrusion pressuresl86401with those predicted by the models of Pugh304 andAvitzur289396reviewed above assuming differentvalues for the coefficient of friction 1 It appears thatthe initial high level of work hardening in suchcompositesI86187192provides a considerable diver-gence from the values for extrusion pressure predictedby the models based on non-work hardening mater-ials while the monolithic X2080AI which exhibitslower work hardening extrudes at pressures moreclosely estimated by the models for a non-workhardening material Clearly more work is neededover a wider range of conditions (eg matrix alloysreinforcement sizes shapes volume fraction) in orderto support the generality of such observationsDamage to the reinforcement was shown to affect themodulus strength and ductility of the extrudate inthose studies401while the superimposition of hydro-static pressure facilitated deformation

Comparatively fewer studies have been conductedto determine the effects of superimposed pressureon the formability of intermetallics or materialsbased on intermetallic compounds Recent worksconducted on both NiAI and TiAI (Refs 104154 164 301) have revealed significant effects ofsuperimposed pressure on both the formability andthe mechanical properties of the hydrostaticallyextruded billet Polycrystalline NiAI typically exhib-its low ductility (eg fracture strain lt 500) andfracture toughness (eg lt 5 MPa m12) at roomtemperature with a ductile to brittle transitiontemperature (DBTT) of ro 300degC (Refs 418 419)The observation of significant pressure inducedductility increases outlined aboveI55-157161163401combined with a beneficial change in fracture mech-anism from intergranular + cleavage to intergranu-lar + quasicleavage suggested that hydrostaticextrusion could be utilised to deformation pro-cess such material at temperatures near the DBTTAlthough hydrostatic extrusion (with backpressure)of NiAI at 25degC exhibited excessive billet crackingsimilar extrusion conditions conducted on NiAI at300degC were successful154 The ability to hydro-statically extrude NiAI at such low temperaturesenabled the retention of a beneficial dislocation sub-structure and a change in texture from the starting

---4Jlrn

--- 37 Jlrn

1

1 1

1 I

--_ _ __ _-----__----__ _ __ _--------

110 800tJI

100

gti~700 eoOr) ~~ ~ar 90 94 Jlrn

o 0 600 ar= omiddot

rIJ 80 ~ =rIJ 37 17 12l-lm rIJQJ rIJ

500 QJ~

70 Monolithic ~

QJ X2080S 400 QJ

60 ceo e-= D eoU -=50 300 U

0(a) bull40 200050 150 250 350 450 550

Ram Travel em

pound=000

140

-= 120OJeClj 100~l-lt0~= 80~~0 60

Clj~~ 40l-ltU

~ 20(b)

0000 01 02 03 04 05 06 07 08

Strain51 a Effects of reinforcement size on chamber

pressure V ram travel for hydrostatic extru-sion of aluminium composites addition ofreinforcement and decreasing reinforcementsize increased extrusion pressure andb damage assessment as function of extrusionstrain for hydrostatically extrudedmaterials 186187

Table 5 Comparison of hydrostatic extrusion pressures obtained186187 for monolithic 2080AI and 2080composites containing different size SiCp to model predictions28929o329396

Avitzur - equation (20)jnon-work hardening

Predicted extrusion pressure MPa

Pugh - equation (16)t Pugh - equation (19)j

Extrusion pressurework hardening non-work hardening

Material MPa J1~O2 J1=O3 J1=02 J1=03

Monolithic X2080AI 476 654 771 557 663X2080AI-15SiCp(SiCp size)

4~m 648-662 698 824 608 7249~m 648-676 695 820 607 723

12 ~m 572 661 780 579 68917 ~m 552-559 653 771 579 68937 ~m 552-579 615 725 558 665

J1=02

559

611610581581561

J1=03

656

717715682682658

AI-364Cu-175Mg-035Zr-0027Fe-003Mn-0025Si wt-t u = (UO1y + UTS)2ju=uy

International Materials Reviews 1998 Vol 43 NO4

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

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404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

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411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

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414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

International Materials Reviews 1998 Vol 43 No4

Page 37: Effects of Hydro Static Pressure on Mechanical

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Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 181

Ex Steels Al alloys Pure cubic metals

53 Summary plot on effects of pressure on yieldstrength of inorganic materials

Inhomogeneous MatlsComposites lt~~i~

2$661-10 ~

IsotropiC IHortlo~eneous

15

20

05

2 Inhomogeneous Materials(i) removal of yield point for materials that exhibit aremoval of yield point due to pressure inducedgeneration of mobile dislocations the yield strengthgenerally decreases with increasing pressureEx Fe Cr W NiAI

(ii) compositesother inhomogeneous systemsthe increase in yield strength with pressure is due tothe generation of dislocations at the reinforcementmatrixinterfaces and to the suppression of damage associatedwith the reinforcement in composites Relaxation ofresidual stress and decreased constraint may reduce theflow stressEx 6061 Al-AI203 AZ91-SiCp Cd Zn

00o 500 1000 1500

Superimposed Hydrostatic Pressure MPa

1 IsotropicHomogeneous MaterialsHydrostatic pressure has no effect on yield strengthas predicted by various yield criterion egthe von Mises yield criterion

CJy

= ~[(CJI -CJ2)2 +(CJ2 -CJJ)2 +(CJ) -CJ)2r2

while additionally providing important input on theprocessing conditions (ie stress state) required todeform such materials successfully Such informationshould be of general interest regardless of the type offorming operation (eg extrusion forging drawingrolling metal forming) under consideration whilealso providing fundamental input on the effects ofchanges in stress state in the flow and fracture behav-iour of materials Finally it is also clear that theeffectiveness of changes in stress state on the ductilitytoughness and formability are critically dependenton the operative fracture micromechanisms whichare controlled by a variety of microstructural features

AcknowledgementsOne of the authors (JJL) would like to acknowledgethe assistance and support of numerous students andcolleagues who have contributed to this effort Theoriginal high pressure testing facility at Case WesternReserve University (CWRU) was conducted underthe direction of S V Radcliffe and H Ll D Pughthe latter partially supported on an extended visit to

International Materials Reviews 1998 Vol 43 NO4

35 Ell ~-5 30 ~ Q 25 eJ)

rJ R curve ~

rIl 20 behaviour 00C)fIJ 0

= 15 ~0 Hydrostatically gtr-~ 10 extruded at 300degCa ceJ c=J D ~~ 5l-o ~ ~

Cast and extruded PM0 00

0 100 200 300 400 500 0

~Strength MPa gt

material154161162 Both the strength (hardness) andtoughness were increased in the extrudate154 Thestrength vas increased from 200 to 400 MPa whilethe toughness increased from 5 to -12 MPa m12bull Inaddition R curve behaviour was exhibited by thehydrostatically extruded NiAI with a peak toughnessof -28 MPa m 12 as summarised in Fig 52 Suchchanges in strength and toughness were accompaniedby a complete change in the fracture mechanism ofNiAI (Ref 154) Preliminary experiments on TiAI(Refs 165 301) hot worked with superimposed press-ure at higher temperatures have also shown thatpressure inhibits cracking in the deformation pro-cessed material though the resulting properties werenot measured in those works

52 Fracture toughness-strength combination ofhydrostatically extruded NiAI (Ref 154)

SummaryThis review has provided an overview of the obser-vations on the effects of superimposed pressure onthe yield strength fracture strain and fracture stressrespectively of a variety of materials while specificinformation on a large number of materials is pro-vided in figures throughout this review Figures 53-55are provided as a summary of the general observationsfor each of the respective properties Broad classes ofbehaviour are represented in Figs 53-55 and includethe key features controlling the specific propertysummarised as well as some specific examples ofmaterials which exhibit such behaviour Althoughno similar summary is presented for the factorscontrolling the deformability formability the datasummarised in Figs 53-55 do provide importantinformation on the effectiveness of changes in stressstate on both the flow and fracture behaviour Suchinformation has been used to deformation processboth conventional and advanced structural materialsWhile the superimposition of pressure has been shownto improve the processability of a wide range ofmaterials property enhancements beyond thosecurrently obtained with conventional processingare also being recorded for materials processedvia these means This would appear to present anumber of unique opportunities for improving theprocessingperformance characteristics of a numberof conventional and advanced structural materials

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

J-o

00~ 30J-oaCJ~J-o 20~~=J-o

E-t 10

000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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182 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

50

=40

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00~ 30J-oaCJ~J-o 20~~=J-o

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000 500 1000 1500 2000 2500

~ 1200~~VJ~ 1000VJ~J-o

~ 800~J-oaCJ 600~J-o~5 400~~=~ 200cU

200 400 600 800 1000 1200

Superimposed Hydrostatic Pressure MPa

1 Failure via Microvoid Coalescence(MVC - Figs 16c and 17c)

Hydrostatic pressure has been found to inhibit MVCwhich consists of void nucleation void growth andvoid coalescence Pressure has been shown to inhibitvoid nucleation while it is known that void growth iscontrolled by am The increase of fracture strainwith pressure varies with material strength andmicrostructural changesEx Steels Al alloys Cu alloys Metal matrix composites

2 Failure via Shear or Ductile Rupture(Figs 16d 16e and 17d-g)

The ductility of materials that fail via shear or ductilerupture are generally insensitive to superimposed hydrostaticpressure At very high pressure levels many materials thattypically fail via MVC may exhibit a fracture mode transitionand subsequently fail via intense shear or ductile ruptureIn such cases the MVC process is entirely suppressedand the material exhibits no further increases in ductility withfurther increases in pressureEx 7075AI-T4 6061AI a-brass amorphous metals

54 Summary plot on effects of pressure onfracture strain of inorganic materials

CWRU by an endowment from Republic Steel IncMore recent students and research associates associ-ated with the high pressure testing facility at CWR Uwho have directly or indirectly contributed to thegeneration and analysis of such data the modificationand upgrading of equipment and have contributedto the authors understanding of such phenomenainclude D S Liu C Liu M ManoharanR W Margevicius J D Rigney B BergerP Harwood T M Osman E 1 HilinskiY Esmaeilpour A L Grow A Vaidya P M SinghJ Zhang P Lowhaphandu S Patankar andS Solvyev Excellent technical support in the gener-ation of such data was provided by D Howe andC Tuma while the design and construction of a gasbased high pressure rig at CWRU was provided byM Costantino and P Harwood of the LawrenceLivermore National Laboratory Colleagues whohave provided useful technical discussions on pressureeffects and testing include A Argon A WThompson F P Bullen R Ballarini A R AustenE Baer A H Heuer V Prakash J D EmburyR O Ritchie J F Knott M Costantino M SPaterson J R Rice S Suresh S Porowski andO Richmond Financial support for equipment used

International Materials Reviews 1998 Vol 43 NO4

Superimposed Hydrostatic Pressure MPa

1 Brittle Materials(i) propagation-controlled fracture the fracture stress of manybrittle materials can be described by the maximum principalstress criterion a material will fracture when the maximumprincipal stress reaches the brittle fracture stress This isevidenced by a one-to-one increase in fracture stress withthe superimposed hydrostatic pressureEx Cast and extruded NiAI Ni3AI W

(ii) nucleation controlled fracture in such cases thenucleation event triggers catastrophic fracture Fracturenucleation events in such cases are not necessarily highlydilatant processes Thus increases in pressure often have littleeffect on the ductility and fracture stress until very high levelsof pressures are attainedEx Ceramics MgO NiAI W Cast Iron Mg Zn

2 Quasi-Brittle MaterialsQuasi-brittle materials such as metal matrix composites alsoexhibit a linear increase in fracture stress with increasinghydrostatic pressure However the increase in fracture stressis often less than a one-to-one response The behaviour is notdescribed by a simple maximum stress criterionEx Discontinuously reinforced metal matrix composites

55 Summary plot on effects of pressure onfracture stress of inorganic materials

at CWRU has been provided by DARPA-ONR-N00013-86-K-0777 NSF-PYI-DMR-89-58326NSF-DMI-95 12296 the Case School of Engineer-ing and Alcoa Support for experimentation wasprovided by DARPA-ONR-N00013-86-K-0777NSF-PYI-DMR-89-58326 Alcoa Alcan AFOSR-F49420-96-1-0228 ONR-NOOOl4-91-J-1370 andONR-N00014-99-1-0327 The donation of a highpressure rig by O Richmond (Alcoa) is gratefullyacknowledged Supply of intermetal1ic materials byI E Locci R D Noebe and R Darolia as appreci-ated as was the supply of various composite materialsby W H Hunt Jr and D J Lloyd Thanks are alsoextended to S Fishman for suggesting that such areview be considered for International MaterialsReviews (IMR) and to G Yoder and the IMR com-mittee for their patience in receiving the manuscript

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262 K R s s KEKULAWALA M S PATERSON and J N BOLAND

in Mechanical behavior of crystal rocks GeophysicalMonograph 24 1981 Washington DC American Geo-physics Union

263 D L KOHLSTEDT and P N CHOPRA in Methods of experimentalphysics (ed C G Sammis et al) 57 1987 Orlando FLAcademic Press

264 M MADON and 1 P POIRIER Science 1980 207 66265 K R McCLAY J Geol Soc London 1977 134 57266 K MOGI Bull Earthquake Res Inst 196644215267 s A F MURRELL in Proc 5th Symp on Rock mechanics

(ed C Fairhurst) 563 1983 Pergamon Press268 M S PATERSON Proc Roy Soc London 1963 A271 57269 M S PATERSON J Inst Eng Aust 1964 36 23270 M S PATERSON J Geophys 1967 14 13271 M S PATERSON Int J Rock Mech Min Sci 1970 7 517272 M S PATERSON Rev Geophys Space Phys 1973 11 355273 M S PATERSON Experimental rock deformation - the brittle

field 1978 Berlin Springer-Verlag274 M S PATERSON High Temp-High Press 1982 14 315275 M S PATERSON Geophys Monogr 199056 187276 1 P POIRIER C SOTIN and 1 PEYRONNEAU Nature 1981

292225277 J P POIRIER Creep of crystals 1985 Cambridge Cambridge

University Press278 J TULLIS G L SHELTON and R A YUND Bull Mineral 1979

102 110279 T E TULLIS and J TULLIS Geophys Monogr 1986 36 297280 D H ZEUCH and H W GREEN Tectonophysics 1984 110 233281 K L De VRIES and P GIBBS J Appl Phys 1963 34 3119282 K L De VRIES G S BAKER and P GIBBS J Appl Phys 1963

342254283 K L De VRIES G S BAKER and P GIBBS J Appl Phys 1963

342258284 S KARATO M TORIUMI and T FUJII in High pressure research

in geophysics (ed S Akimoto et al) 171 1982 TokyoCenter of Academic Publications

285 R W KEYES in Solid under pressure (ed W Paul et al)1963 New York McGraw-Hill

286 P G McCORMICK and A L RUOFF J Appl Phys 1969404812287 A R AUSTEN and w L HUTCHINSON in Rapidly solidified

materials properties and processing Proc 2nd Int Conf onRapidly Solidified Materials San Diego CA 1989 ASMInternational

288 A R AUSTEN and w L HUTCHINSON Adv Cryogenic Eng A1990 36 741

289 B AVITZUR J Eng Ind (Trans ASME Series B) 1965 87 487290 B I BERESNEV L F VERESHCHAGIN and Y N RYABININ Izv

Akad Nauk SSSR Mekh i Mashin 1959 7 128291 B I BERESNEV L F VERESHCHAGIN and Y N RYABININ Inzh-

jiz Zh 1960 3 43292 B I BERESNEV D K BULYCHEV and K P RODIONOV Fiz Met

Metalloved 1961 11 115293 A BOBROWSKY E A STACK and A AUSTEN ASTM Technical

paper no SP65-33 ASTM Philadelphia PA294 A BOBROWSKY and E A STACK in Symp on Metallurgy at

high pressures and high temperatures Dallas TX (ed K AGschneider Jr et al) 1964 Gordon and Breach Science

295 D K BULYCHEV and B I BERESNEV Fiz Met Metalloved1962 13 942

296 L H BUTLER J Inst Met 1964-65 93 123297 J M GOODES Wire Ind 197542530298 R MOLYNEUX Wire Ind 1977 44 234299 c J NOLAN and T E DAVIDSON Trans ASM 196962271300 J A PARDOE Wire J 1978 11 (7) 82301 O PAWELSKI K E HAGEDORN and R HOP Steel Res 1994

65326302 H Ll D PUGH in Proc Int Production Engineering Conf

Pittsburgh PA 1963 ASME 394303 H Ll D PUGH New Scientist Apr 1963 (333) 4304 H Ll D PUGH J Mech Eng Soc 19646362305 H Ll D PUGH and A H LOW J Inst Met 1964-65 93 201306 H Ll D PUGH Bullied Memorial Lectures Nos 3 and 4

University of Nottingham UK 1965307 R N RANDALL D M DAVIES and 1 M SIERGIEJ Mod Met

1962 17 68308 Y N RYABININ B I BERESNEV and B P DEMYASHKEVIDH Fiz

Met Metalloved 1961 11 630309 H K SLATER Wire J 1979 12 (2) 76

International Materials Reviews 1998 Vol 43 NO4

310 E G THOMSEN J Inst Mech Eng 195777311 J c UY c J NOLAN and T E DAVIDSON Trans ASM 1967

60 693312 w G VOORHES Light Met Age 1978 18313 J JUNG Philos Mag 1981 43A 1057314 v T SHMATOV Fiz Met Metalloved 1973 35 277315 T CHRISTMAN A NEEDLEMAN S NUTT and s SURESH Mater

Sci Eng 1989 AI07 49316 T CHRISTMAN A NEEDLEMAN and s SURESH Acta Metall

1989 37 3029317 T CHRISTMAN J LLORCA S SURESH and A NEEDLEMAN

in Inelastic deformation of composite materials (edG J Dvorak) 309 1990 New York Springer-Verlag

318 G M GEJIN The effects of superimposed hydrostatic pressureon deformation of an idealized metal matrix composite MSthesis Department of Civil Engineering Case Western ReserveUniversity Cleveland OH 1992

319 H LUO R BALLARINI and J 1 LEWANDOWSKI in Mechanicsof composites at elevated and cryogenic temperatures (edS N Singhal et al) 195 1991 New York ASME

320 H LUO R BALLARINI and J J LEWANDOWSKI J ComposMater 1992 26 1945

321 P B BOWDEN and 1 A JUKES J Mater Sci 1972 7 52322 J c M LI and 1 B c wu J Mater Sci 1976 11 445323 L A DAVIES and s KAVESH J Mater Sci 1975 10 453324 J J LEWANDOWSKI P LOWHAPHANDU and s MONTGOMERY

Scr Metall Mater 1998 in press325 G T GRAY in High pressure shock compression of solids

(ed J R Asay et al) 187 1993 New York Springer-Verlag326 D H NEWHALL and L H ABBOT Proc Inst Mech Eng

196768 182 288327 M I EREMETS High pressure experimental method 1996

Oxford Oxford University Press328 s H GELLES Rev Sci Instr 1968 39 12329 F BIRCH E C ROBERTSON and J CLARK Ind Eng Chern

1957 49 1965330 D CARPENTER and M CONTRE Rev Sci Instr 1970 41 189331 1 W JACKSON and M WAXMAN in High-pressure measure-

ment (ed A H Giardini et al) 39 1963 LondonButterworth

332 D H NEWHALL Instr Control Syst 1962 35 103333 J E HANAFEE and s V RADCLIFFE Rev Sci Inst 196738 328334 M COSTANTINO P LOWHAPHANDU P HARWOOD P M SINGH

and J J LEWANDOWSKI Unpublished research Case WesternReserve University Cleveland OH 1994

335 s M DORAIVELU H L GEGEL J S GUNASEKERA J C MALAS

and J T MORGAN Int J Mech Sci 198426 527336 E J HILINSKI J J LEWANDOWSKI and P T WANG in Aluminum

and magnesium for automotive applications (edJ D Bryant) 189 1996 Warrendale PA TMS-AIME

337 M F ASHBY S H GELLES and L E TANNER Phios Mag 196919 757

338 A H COTTRELL Theory of crystal dislocations 1964 NewYork Gordon and Breach

339 T E DAVIDSON J C UY and A P LEE Trans AIME 1965233820

340 J w SWEGLE J Appl Phys 1980 51 2574341 E J HILINSKI J J LEWANDOWSKI T J RODJOM and P T WANG

in 1994 World PM congress (ed C Lall et al) 259 1994Princeton NJ MPIF

342 E J HILINSKI 1 J LEWANDOWSKI T J RODJOM and P T WANG

in 1994 World PM congress (ed C Lall et al) 269 1994Princeton NJ MPIF

343 c LIU and J J LEWANDOWSKI Unpublished research CaseWestern Reserve University Cleveland OH 1991

344 c LIU G MICHAL and J J LEWANDOWSKI in Residual stressesin composites measurement modeling and effects on thermo-mechanical behavior (ed E V Barrera et al) 1993 DenverCO TMS

345 P F THOMASON Ductile fracture of metals 1990 New YorkPergamon Press

346 J F KNOTT Fundamentals of fracture mechanics 1973London Butterworths

347 A W THOMPSON and J F KNOTT Metall Trans A 199324A523

348 R O RITCHIE and A W THOMPSON Metall Trans A 198516A233

349 F A McCLINTOCK and A S ARGON Mechanical behaviour ofmaterials 1966 Reading MA Addison-Wesley

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350 R O RITCHIE J F KNOTT and J R RICE J Mech Phys Solids1973 21 395

351 M F ASHBY J D EMBURY S H COOKSLEY and D TEIRLINCK

SCI Metall 1985 19 385352 M A MEYERS and K K CHAWLA Mechanical behavior of

materials 1998 Upper Saddle River NJ Prentice Hall353 A SAMANT and 1 1 LEWANDOWSKI Metall Mater Trans A

1997 28A 2297354 J1 LEWANDOWSKI and J F KNOTT in Proc 7th Int Conf on

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412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

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Rev 1993 38 193

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186 Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials

262 K R s s KEKULAWALA M S PATERSON and J N BOLAND

in Mechanical behavior of crystal rocks GeophysicalMonograph 24 1981 Washington DC American Geo-physics Union

263 D L KOHLSTEDT and P N CHOPRA in Methods of experimentalphysics (ed C G Sammis et al) 57 1987 Orlando FLAcademic Press

264 M MADON and 1 P POIRIER Science 1980 207 66265 K R McCLAY J Geol Soc London 1977 134 57266 K MOGI Bull Earthquake Res Inst 196644215267 s A F MURRELL in Proc 5th Symp on Rock mechanics

(ed C Fairhurst) 563 1983 Pergamon Press268 M S PATERSON Proc Roy Soc London 1963 A271 57269 M S PATERSON J Inst Eng Aust 1964 36 23270 M S PATERSON J Geophys 1967 14 13271 M S PATERSON Int J Rock Mech Min Sci 1970 7 517272 M S PATERSON Rev Geophys Space Phys 1973 11 355273 M S PATERSON Experimental rock deformation - the brittle

field 1978 Berlin Springer-Verlag274 M S PATERSON High Temp-High Press 1982 14 315275 M S PATERSON Geophys Monogr 199056 187276 1 P POIRIER C SOTIN and 1 PEYRONNEAU Nature 1981

292225277 J P POIRIER Creep of crystals 1985 Cambridge Cambridge

University Press278 J TULLIS G L SHELTON and R A YUND Bull Mineral 1979

102 110279 T E TULLIS and J TULLIS Geophys Monogr 1986 36 297280 D H ZEUCH and H W GREEN Tectonophysics 1984 110 233281 K L De VRIES and P GIBBS J Appl Phys 1963 34 3119282 K L De VRIES G S BAKER and P GIBBS J Appl Phys 1963

342254283 K L De VRIES G S BAKER and P GIBBS J Appl Phys 1963

342258284 S KARATO M TORIUMI and T FUJII in High pressure research

in geophysics (ed S Akimoto et al) 171 1982 TokyoCenter of Academic Publications

285 R W KEYES in Solid under pressure (ed W Paul et al)1963 New York McGraw-Hill

286 P G McCORMICK and A L RUOFF J Appl Phys 1969404812287 A R AUSTEN and w L HUTCHINSON in Rapidly solidified

materials properties and processing Proc 2nd Int Conf onRapidly Solidified Materials San Diego CA 1989 ASMInternational

288 A R AUSTEN and w L HUTCHINSON Adv Cryogenic Eng A1990 36 741

289 B AVITZUR J Eng Ind (Trans ASME Series B) 1965 87 487290 B I BERESNEV L F VERESHCHAGIN and Y N RYABININ Izv

Akad Nauk SSSR Mekh i Mashin 1959 7 128291 B I BERESNEV L F VERESHCHAGIN and Y N RYABININ Inzh-

jiz Zh 1960 3 43292 B I BERESNEV D K BULYCHEV and K P RODIONOV Fiz Met

Metalloved 1961 11 115293 A BOBROWSKY E A STACK and A AUSTEN ASTM Technical

paper no SP65-33 ASTM Philadelphia PA294 A BOBROWSKY and E A STACK in Symp on Metallurgy at

high pressures and high temperatures Dallas TX (ed K AGschneider Jr et al) 1964 Gordon and Breach Science

295 D K BULYCHEV and B I BERESNEV Fiz Met Metalloved1962 13 942

296 L H BUTLER J Inst Met 1964-65 93 123297 J M GOODES Wire Ind 197542530298 R MOLYNEUX Wire Ind 1977 44 234299 c J NOLAN and T E DAVIDSON Trans ASM 196962271300 J A PARDOE Wire J 1978 11 (7) 82301 O PAWELSKI K E HAGEDORN and R HOP Steel Res 1994

65326302 H Ll D PUGH in Proc Int Production Engineering Conf

Pittsburgh PA 1963 ASME 394303 H Ll D PUGH New Scientist Apr 1963 (333) 4304 H Ll D PUGH J Mech Eng Soc 19646362305 H Ll D PUGH and A H LOW J Inst Met 1964-65 93 201306 H Ll D PUGH Bullied Memorial Lectures Nos 3 and 4

University of Nottingham UK 1965307 R N RANDALL D M DAVIES and 1 M SIERGIEJ Mod Met

1962 17 68308 Y N RYABININ B I BERESNEV and B P DEMYASHKEVIDH Fiz

Met Metalloved 1961 11 630309 H K SLATER Wire J 1979 12 (2) 76

International Materials Reviews 1998 Vol 43 NO4

310 E G THOMSEN J Inst Mech Eng 195777311 J c UY c J NOLAN and T E DAVIDSON Trans ASM 1967

60 693312 w G VOORHES Light Met Age 1978 18313 J JUNG Philos Mag 1981 43A 1057314 v T SHMATOV Fiz Met Metalloved 1973 35 277315 T CHRISTMAN A NEEDLEMAN S NUTT and s SURESH Mater

Sci Eng 1989 AI07 49316 T CHRISTMAN A NEEDLEMAN and s SURESH Acta Metall

1989 37 3029317 T CHRISTMAN J LLORCA S SURESH and A NEEDLEMAN

in Inelastic deformation of composite materials (edG J Dvorak) 309 1990 New York Springer-Verlag

318 G M GEJIN The effects of superimposed hydrostatic pressureon deformation of an idealized metal matrix composite MSthesis Department of Civil Engineering Case Western ReserveUniversity Cleveland OH 1992

319 H LUO R BALLARINI and J 1 LEWANDOWSKI in Mechanicsof composites at elevated and cryogenic temperatures (edS N Singhal et al) 195 1991 New York ASME

320 H LUO R BALLARINI and J J LEWANDOWSKI J ComposMater 1992 26 1945

321 P B BOWDEN and 1 A JUKES J Mater Sci 1972 7 52322 J c M LI and 1 B c wu J Mater Sci 1976 11 445323 L A DAVIES and s KAVESH J Mater Sci 1975 10 453324 J J LEWANDOWSKI P LOWHAPHANDU and s MONTGOMERY

Scr Metall Mater 1998 in press325 G T GRAY in High pressure shock compression of solids

(ed J R Asay et al) 187 1993 New York Springer-Verlag326 D H NEWHALL and L H ABBOT Proc Inst Mech Eng

196768 182 288327 M I EREMETS High pressure experimental method 1996

Oxford Oxford University Press328 s H GELLES Rev Sci Instr 1968 39 12329 F BIRCH E C ROBERTSON and J CLARK Ind Eng Chern

1957 49 1965330 D CARPENTER and M CONTRE Rev Sci Instr 1970 41 189331 1 W JACKSON and M WAXMAN in High-pressure measure-

ment (ed A H Giardini et al) 39 1963 LondonButterworth

332 D H NEWHALL Instr Control Syst 1962 35 103333 J E HANAFEE and s V RADCLIFFE Rev Sci Inst 196738 328334 M COSTANTINO P LOWHAPHANDU P HARWOOD P M SINGH

and J J LEWANDOWSKI Unpublished research Case WesternReserve University Cleveland OH 1994

335 s M DORAIVELU H L GEGEL J S GUNASEKERA J C MALAS

and J T MORGAN Int J Mech Sci 198426 527336 E J HILINSKI J J LEWANDOWSKI and P T WANG in Aluminum

and magnesium for automotive applications (edJ D Bryant) 189 1996 Warrendale PA TMS-AIME

337 M F ASHBY S H GELLES and L E TANNER Phios Mag 196919 757

338 A H COTTRELL Theory of crystal dislocations 1964 NewYork Gordon and Breach

339 T E DAVIDSON J C UY and A P LEE Trans AIME 1965233820

340 J w SWEGLE J Appl Phys 1980 51 2574341 E J HILINSKI J J LEWANDOWSKI T J RODJOM and P T WANG

in 1994 World PM congress (ed C Lall et al) 259 1994Princeton NJ MPIF

342 E J HILINSKI 1 J LEWANDOWSKI T J RODJOM and P T WANG

in 1994 World PM congress (ed C Lall et al) 269 1994Princeton NJ MPIF

343 c LIU and J J LEWANDOWSKI Unpublished research CaseWestern Reserve University Cleveland OH 1991

344 c LIU G MICHAL and J J LEWANDOWSKI in Residual stressesin composites measurement modeling and effects on thermo-mechanical behavior (ed E V Barrera et al) 1993 DenverCO TMS

345 P F THOMASON Ductile fracture of metals 1990 New YorkPergamon Press

346 J F KNOTT Fundamentals of fracture mechanics 1973London Butterworths

347 A W THOMPSON and J F KNOTT Metall Trans A 199324A523

348 R O RITCHIE and A W THOMPSON Metall Trans A 198516A233

349 F A McCLINTOCK and A S ARGON Mechanical behaviour ofmaterials 1966 Reading MA Addison-Wesley

Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd

Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 187

350 R O RITCHIE J F KNOTT and J R RICE J Mech Phys Solids1973 21 395

351 M F ASHBY J D EMBURY S H COOKSLEY and D TEIRLINCK

SCI Metall 1985 19 385352 M A MEYERS and K K CHAWLA Mechanical behavior of

materials 1998 Upper Saddle River NJ Prentice Hall353 A SAMANT and 1 1 LEWANDOWSKI Metall Mater Trans A

1997 28A 2297354 J1 LEWANDOWSKI and J F KNOTT in Proc 7th Int Conf on

Strength of metals and alloys - ICSMA 7 Montreal Aug1985 1193 1985 New York Pergamon Press

355 J R LOW in Relation of properties to microstructure 1631953 Novelty OH ASM

356 A N STROH Adv Phys 1957 6418357 A N STROH Phios Mag 1958 3 597358 1 FREIDEL Dislocations 1964 New York Pergamon Press359 1 F KNOTT and A H COTTRELL J Iron Steel Inst 1963

201249360 J F K~OTT J Iron Steel Inst 1966 204 104361 1 F KOTT J Iron Steel lISt 1966 204 1014362 J F K~OTT J Iron Steel Inst 1967 205 288363 OROWAN Trans Inst Eng Shipbuilders Scotland 194589 1165364 N N DAVIDENKOV Dinamicheskaya ispytania metallov 1936

Moscow USSR365 1 1 LEWANDOWSKI and A W THOMPSON Metall Trans 1986

17A 1769366 J J LEWANDOWSKI and A W THOMPSON Acta Metall 1987

35 1453367 A SAMANT and 1 J LEWANDOWSKI Metall Mater Trans A

1997 28A 389368 D TEIRLINCK F ZOK J D EMBURY and M F ASHBY Acta

Metall 1988 36 1213369 D TEIRLINCK M F ASHBY and J D EMBURY in Advances in

fracture research - ICF 6 New Delhi India Dec 1984 105New York Pergamon Press

370 w M GARRISON Jr and N R MOODY J Phys Chem Solids1987 48 1035

371 A W THOMPSON Metall Trans A 1987 18A 1877372 L M BROWN and J D EMBURY in Proc 3rd Int Conf on

Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

374 s H GOOD and L M BROWN Acta Metall 197927 1375 L M BROWN and w M STOBBS Phios Mag 197634 351376 P F THOMASON Ductile fracture of metals 94 1990 New

York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

International Materials Reviews 1998 Vol 43 No4

Page 43: Effects of Hydro Static Pressure on Mechanical

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lishe

d by

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ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd

Lewandowski and Lowhaphandu Effects of hydrostatic pressure on materials 187

350 R O RITCHIE J F KNOTT and J R RICE J Mech Phys Solids1973 21 395

351 M F ASHBY J D EMBURY S H COOKSLEY and D TEIRLINCK

SCI Metall 1985 19 385352 M A MEYERS and K K CHAWLA Mechanical behavior of

materials 1998 Upper Saddle River NJ Prentice Hall353 A SAMANT and 1 1 LEWANDOWSKI Metall Mater Trans A

1997 28A 2297354 J1 LEWANDOWSKI and J F KNOTT in Proc 7th Int Conf on

Strength of metals and alloys - ICSMA 7 Montreal Aug1985 1193 1985 New York Pergamon Press

355 J R LOW in Relation of properties to microstructure 1631953 Novelty OH ASM

356 A N STROH Adv Phys 1957 6418357 A N STROH Phios Mag 1958 3 597358 1 FREIDEL Dislocations 1964 New York Pergamon Press359 1 F KNOTT and A H COTTRELL J Iron Steel Inst 1963

201249360 J F K~OTT J Iron Steel Inst 1966 204 104361 1 F KOTT J Iron Steel lISt 1966 204 1014362 J F K~OTT J Iron Steel Inst 1967 205 288363 OROWAN Trans Inst Eng Shipbuilders Scotland 194589 1165364 N N DAVIDENKOV Dinamicheskaya ispytania metallov 1936

Moscow USSR365 1 1 LEWANDOWSKI and A W THOMPSON Metall Trans 1986

17A 1769366 J J LEWANDOWSKI and A W THOMPSON Acta Metall 1987

35 1453367 A SAMANT and 1 J LEWANDOWSKI Metall Mater Trans A

1997 28A 389368 D TEIRLINCK F ZOK J D EMBURY and M F ASHBY Acta

Metall 1988 36 1213369 D TEIRLINCK M F ASHBY and J D EMBURY in Advances in

fracture research - ICF 6 New Delhi India Dec 1984 105New York Pergamon Press

370 w M GARRISON Jr and N R MOODY J Phys Chem Solids1987 48 1035

371 A W THOMPSON Metall Trans A 1987 18A 1877372 L M BROWN and J D EMBURY in Proc 3rd Int Conf on

Strength of metals and alloys 1975 161 1975 London TheMetals Society and the Iron and Steel Institute

373 A S ARGON J 1M and R SAFOGLU Metall Trans A 19756A825

374 s H GOOD and L M BROWN Acta Metall 197927 1375 L M BROWN and w M STOBBS Phios Mag 197634 351376 P F THOMASON Ductile fracture of metals 94 1990 New

York Pergamon Press377 1 R RICE and D M TRACEY J Mech Phys Solids 1969 17378 F A McCLINTOCK Trans ASME (Series E) 1968 35 363379 D C DRUCKER J Mater 1966 1 872380 c Q CHEN and 1 F KNOTT Met Sci 1981 15 357381 J E KING C P YOU and J F KNOTT Acta Metall 1981

29 1553382 M MANOHARAN J J LEWANDOWSKI and w H HUNT Jr Mater

Sci Eng 1993 A172 63383 P M SINGH and J 1 LEWANDOWSKI SCIMetall Mater 1993

29 199384 P M SINGH and J J LEWANDOWSKI in Intrinsic and extrinsic

fracture mechanisms in inorganic composites (edJ J Lewandowski et al) 57 1995 Warrendale PA TMS

385 J J LEWANDOWSKI C LIU and w H HUNT Jr Mater SciEng 1989 107A 241

386 J 1 LEWANDOWSKI C LIU and w H HUNT Jr in Powdermetallurgy composites (ed P Kumar et al) 117 1987Warrendale PA TMS-AIME

387 1 J LEWANDOWSKI SAMPE Q 1989 20 (2) 33388 J J LEWANDOWSKI and c LIU in Proc Int Conf on Advanced

structural materials Montreal (ed D Wilkinson) 23 1988Pergamon Press

389 G ROZAK J J LEWANDOWSKI J F WALLACE andA ALTMISOGLU J Compos Mater 1992 14 2076

390 G A ROZAK 1 J LEWANDOWSKI and J F WALLACE SAETrans Paper no 930180 1993

391 1 D EMBURY F ZOK D J LAHAIE and w POOLE in Intrinsicand extrinsic fracture mechanism in inorganic compositessystem (ed J J Lewandowski et al) 1 1995 PittsburghPA TMS

392 J R RICE and ~1 A JOHNSON in Inelastic behavior of solids(ed M F Kanninen et al) 641 1970 New York McGraw-Hill

393 G T HAHN and A R ROSENFIELD kfetall Trans A 19756A653

394 w BACKHOFEN Deformation processing 1972 Reading MAAddison- Wesley

395 w F HOSFORD and R ~1 CADDELL Metal forming mechanicsand metallurgy 2nd edn 1993 Englewood Cliffs NJ PTRPrentice Hall

396 B AVITZUR J Eng Ind (Trans ASNIE Series B) 1966 88410

397 B AVITZUR Metal forming process and analysis 1968 NewYork McGraw-Hill

398 H L1 D PUGH in The mechanical behaviour of materialsunder pressure (ed H Ll D Pugh) 391 1970 New YorkElsevier

399 H LI D PUGH Iron and Steel 1972 45 39400 M S OH Q F LIU W Z MISIOLEK A RODRIGUES B AVITZUR

and M R NOTIS J Am Ceram Soc 1989722142401 s N PATANKAR A L GROW R W ~fARGEVICIUS and

J J LEWANDOWSKI in Processing and fabrication of advan-ced materials III (ed V Ravi et al) 733 1994 PittsburghPA TMS

402 B I BERESNEV D K BULYCHEV ~f G GAYDUKOV YEo D

MARTYNOV K P RODIOiOV and YO N RYABININ Fiz vIetMetallov 1964 18 (5) 778

403 D K BULYCHEV B I BERESNEV M G GAYDUKOV yE D

MARTYNOV K P RODIONOV and YO N RYABININ Fiz NfetMetallov 1964 18 (3) 437

404 H-W WAGENER J HATTS and J WOLF J Mater ProcessTechnol 1992 32 451

405 H-W WAGENER and J WOLF J Mater Process Teemol 1stAsia-Pacific Conf on Materials processing 1993 37 253

406 H-W WAGENER and J WOLF Key Eng Mater 1995104-107 99

407 F J FUCHS in Engineering solids under pressure (edH Ll D Pugh) 145 1970 London Institution ofMechanical Engineers

408 J CRAWLEY J A PENNELL and A SAUNDERS Proc Inst MechEng 1967-68 182 180

409 J M ALEXANDER and B LENGYEL Hydrostatic extrusion1971 London Mills and Boon

410 c S COOK R 1 FIORENTINO and A ~f SABROFF in Technicalpaper 64-MD-13 7 1964 Dearborn MI Society ofManufacturing Engineers

411 H LUNDSTROM ASTME Technical paper MF 69-167 ASTMPhiladelphia PA 1969 12

412 w R D WILSON and J A WALOWIT J Lub Technol (TrailSASME F) 1971 93 69

413 S THIRUVARUDCHELVAN and J M ALEXANDER Int J vlachTool Design Res 1971 11 251

414 L F COFFIN and H C ROGERS Trans ASM 1967 60 672415 H C ROGERS Ductility 1968 Cleveland OH ASM416 S N PATANKAR and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998417 S SOLYVEV and J J LEWANDOWSKI Unpublished research

Case Western Reserve University Cleveland OH 1998418 D B MIRACLE Acta Metall Mater 1993 41 649419 R D NOEBE R R BOWMAN and M v NATHAL Int Mater

Rev 1993 38 193

International Materials Reviews 1998 Vol 43 No4