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Wear 269 (2010) 664671
Contents lists available at ScienceDirect
Wear
journa l homepage: www.e lsev ier .co
High te co
Yucel BirMaterials Instit
a r t i c l
Article history:Received 11 MReceived in reAccepted 7
JulAvailable onlin
Keywords:Sliding wearSteelHigh temperatWear testing
nce oot wits in
al maar ac0 C in theese al
1. Introdu
High temmetallic sutemperaturof mechaniicant role of the latter
in high temperature sliding wear wasrst identied by Fink [5]. It is
well known that oxidation leadsto material degradation and
consequently, reduces the materialresistance to wear. However, a
surface oxide may reduce theoxidation rate and help to decrease the
wear loss if it is denseand strongwas discusture wear [reviewed
bpretation o[19].
High temmechanismvery attractfor drive untool materia[22]. The
codeterioratesion of hardcobalt-baseing resistan
Tel.: +90 2E-mail add
traction rraturandir po333
[3337]. It is thus of great technological interest to explore
theirwear resistance at high temperatures. While the ambient
temper-ature wear performance has been investigated in detail,
publishedinformation on the wear performance of these alloys at
high tem-peratures is scarce. Thepresentworkwasundertaken to
investigate
0043-1648/$ doi:10.1016/j.[6,7]. The role of oxide scale in the
wear of metalssed extensively both for ambient and high
tempera-816] while the mechanisms of oxidation wear werey Quinn
[17,18]. Some new approaches on the inter-f oxidation wear
mechanisms have also been proposed
perature wear is identied to be a potential failurefor
thixoforging tools [20,21]. While thixoforging is aive processing
route for the manufacture of steel partsits and chassis components,
it is very demanding onls with high process temperatures involved
(>1300 C)nventional hot work tool steels were shown to
rapidlyunder such severe conditions [2327]. With a disper-carbide
particles in a cobalt-rich solid solution matrix,alloys are
exceptionally good for applications requir-ce to oxidation and wear
[2831]. Ni-base alloys are
62 6773084; fax: +90 262 6412309.ress:
[email protected].
the high temperature sliding wear resistance of Stellite 6
andInconel 617 alloys and rate their performance against that of
theconventional hot work tool steel employed in hot forging of
steelcomponents.
2. Experimental
A CETR Universal Material Tester-2 model ball-on-disc type
tri-bometer (Fig. 1) was used to investigate the high temperature
wearproperties of Inconel 617 and Stellite 6 alloys and X32CrMoV33
hotwork tool steel (Table 1).Wear testswere carried out at 750
Cwitha sliding speed of 0.025m/s, under 5N load for 60min. The
testtemperature was selected with a consideration of the
maximumtemperature achieved at the surface of the die cavity during
steelthixoforming experiments [33]. Since the tool is abraded by
verysmall-Feparticles thatmakeup the solid fractionof the
semi-solidfeedstock, the ball diameter and the applied load were
selected soas toproducea scratching case. A0.001mdiameter
aluminaball ranover disk samples over a circular path having a
diameter of 0.03m.The disc surfaces were ground with a 1000 mesh
grit sandpaper
see front matter 2010 Elsevier B.V. All rights
reserved.wear.2010.07.005mperature sliding wear behaviour of In
ol
ute, Marmara Research Center, 41470 TUBITAK, Kocaeli, Turkey
e i n f o
arch 2010vised form 7 July 2010y 2010e 15 July 2010
ure
a b s t r a c t
The high temperature wear performapared with that of the
X32CrMoV33 hjudged to be very poor due basically towith wear at 750
C leads to substantisufciently ductile to sustain the weInconel 617
and Stellite 6 alloys at 75Inconel 617 andStellite 6 alloys
sustaifor the superior wear resistance of th
ction
perature wear is one of the life-limiting factors whenrfaces are
in repeated contact [13]. High forminges impact the wear behaviour
of tools through losscal strength and enhanced oxidation [4]. The
signif-
also atoxidattempe
Co-for thement [m/locate /wear
nel 617 and Stellite 6 alloys
f Inconel 617 and Stellite 6 alloys was investigated and com-ork
tool steel. The wear performance of the latter at 750 C isferior
oxidation resistance. Extensive oxidation co-occurringterial loss
basically due to the lack of an adhesive oxide scale,tion without
extensive spalling. The wear resistance of thes relatively
superior. The adhesive oxides growing slowly onwear actionwithout
spalling andare claimed tobe responsibleloys at 750 C.
2010 Elsevier B.V. All rights reserved.
ive high temperature materials owing to an excellentesistance,
creep strength and phase stability at highes [32].Ni-based high
temperature alloys were tested recentlytential to withstand the
steel thixoforming environ-6]. Their thermal fatigue performance is
encouraging
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Y. Birol / Wear 269 (2010) 664671 665
Table 1Chemical composition of the X32CrMoV33 hot work tool
steel and Ni- and Co-based high temperature alloys used in the
present work.
Alloy C Si Mn Cr Mo Ni Al Co Cu Nb Ti V W Fe
X32CrMoV33 0.281 0.190 0.200 3.005 2.788 0.221 0.025
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666 Y. Birol / Wear 269 (2010) 664671
Fig. 4. Friction coefcient curves of the X32CrMoV33, Inconel 617
and Stellite 6 disc samples submitted to ball-on-disc sliding wear
test at 750 C.
3. Results and discussion
Two- and three-dimensional prolometer images and two-dimensional
surface proles of the tested surfaces are illustratedin Fig. 2. The
widest and the deepest wear track, and thus the high-
Fig. 5. Opticaldisc samples s
est volume loss occurred in the hot work tool steel. It is clear
fromFig. 2 that the surface of the hot work tool steel disc sample
hasdeteriorated not only inside but also outside the wear track,
due tothe extensive oxidation suffered by this material at the test
tem-perature. The width and the depth of the wear tracks are
relativelysmaller in the Inconel 617 alloy and the smallest in the
Stellite 6alloy. These are consistent with the wear volume loss
measure-ments which clearly identify the hot work tool steel to be
the leastand the Stellite 6 alloy the most resistant to sliding
wear at 750 C(Fig. 3).
The friction coefcients measured during the sliding wear
testsare shown in Fig. 4. The friction coefcient of the X32CrMoV33
hotmicrographs of (a) X32CrMoV33, (b) Inconel 617 and (c) Stellite
6ubmitted to ball-on-disc sliding wear test at 750 C.
Fig. 6. OpticaX32CrMoV33,l micrographs showing transverse
section of the wear track of (a)(b) Inconel 617 and (c) Stellite 6
disc samples.
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Y. Birol / Wear 269 (2010) 664671 667
work tool steel is as low as 0.2 at the start of the test and
increaseswith time to approximately 0.4. The thick oxide layer
formed onthe surface of the tool steel at 750 C is believed to have
served asa lubricant leading to a low friction coefcient initially.
Low fric-tion coefcients are linked with poor adherence and thick
oxidelayers [38,39] which help to enlarge the contact surface
therebydecreasing the strain and thus the friction coefcient [40].
Smallinitial friction coefcient values may also be accounted for by
thesudden loss of strength upon thermal exposure. The decohesion
of
Fig. 7. ScanniStellite 6 disc
oxide scales, generation and accumulation of debris in the
contactzone are responsible for the relatively larger uctuations
and foran ever-increasing friction coefcient. It is inferred from
these fea-tures of the friction coefcient curve that the oxide
layer on the toolsteel disc sample is not stable.
The friction coefcient curves of the Inconel 617 and Stellite
6alloys are markedly different. That of the former is stabilized
at
cannidiscng electron micrographs of (a) X32CrMoV33, (b) Inconel
617 and (c)samples submitted to ball-on-disc sliding wear test at
750 C.
Fig. 8. SStellite 6ng electron micrographs of (a) X32CrMoV33,
(b) Inconel 617 and (c)samples submitted to ball-on-disc sliding
wear test at 750 C.
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668 Y. Birol / Wear 269 (2010) 664671
Fig. 9. Scanning electron micrograph of the glazed layer in
Inconel 617 disc samplesubmitted to ball-on-disc sliding wear test
at 750 C.
approximately 0.24 and remains more or less constant with
slidingtime after an initial running-in period of about 500 s. The
frictioncoefcient of Stellite 6 alloy shows a similar trend but
runs at ahigher value, at approximately 0.48. It is fair to
conclude that thefriction and wear conditions are quite stable in
the Inconel 617 andStellite 6 alloys owing to a stable oxide
layer.
The optical micrographs of the wear tracks are shown in Fig.
5.Interestingly, the microstructural features are readily
identiedon Inconel 617 and Stellite 6 disc samples without the
benet ofchemical etching. This is typical of a well known practice
in met-allography [41] and evidences a thin oxide lm which helps
todelineate the microstructure under cross polarizer. This effect
isnot offered by the hot work tool steel disc sample simply due toa
much thicker oxide all over. Further evidence for the extent
ofoxidation in the three alloys is available in the transverse
sectionsof the wear tracks in the respective disc samples (Fig. 6).
A verythick oxide scale is evident in the hot work tool steel
sample whileoxide lms on the Inconel 617 and Stellite 6 alloys are
apparently
Fig. 10. Elemesamples submnt distribution proles (a, b, c) and
oxygen distribution proles (d, e, f) across the wear titted to
ball-on-disc sliding wear test at 750 C.racks of (a, d) X32CrMoV33,
(b, e) Inconel 617 and (c, f) Stellite 6 disc
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Y. Birol / Wear 269 (2010) 664671 669
too thin to be resolved with an optical microscope. The former
hasapparently failed to sustain the wear loading and has fractured
toproduce oxide debris in the wear track.
Abrasivewearwith grooving in the slidingdirection, a very
thickoxide layer and an appreciable quantity of debris accumulated
atthe edges of the track were the basic wear features for the hot
worktool steel (Figs. 7 and 8). The oxides along the edges of the
weartrack were inferred from their colour to be hematite, in
contrast tothe dark-coloured magnetite covering the disc surface.
The oxidedebris was apparently carried to the edge of the track by
the alu-minaballwhere it has oxidised again.Magnetite
reactswithoxygento produce hematite. Oxidation, fresh surface
generation via frac-
ture and removal of the surface oxides inside the wear track
andreoxidation of the fresh surface are claimed to be responsible
forthe substantial wear loss suffered by the hot work tool steel.
Theremoved oxide itself might have acted as an abrasive agent
whilststill within thewear interface producing an abrasive element
in thewear of X32CrMoV33. Fig. 7a suggests that this is a likely
mecha-nism when the oxide debris does not readily sinter to form a
glazeand act as a third body abrasive [11].
The features of the worn surfaces of the Inconel 617 and
Stellite6 alloys are markedly different (Figs. 7 and 8). The oxides
on theInconel 617 and Stellite 6 samples are very thin. The oxide
debris,although much less in quantity, was somehow retained inside
the
Fig. 11. 6 discXRD spectra obtained from the tested surfaces of
(a) X32CrMoV33 and (b) Stellite samples submitted to ball-on-disc
sliding wear test at 750 C.
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670 Y. Birol / Wear 269 (2010) 664671
wear track and was compacted into a glazed surface [2,42,43].
Thehigh hardness of the alumina ball and its capacity to form
largegroves so as to retain the oxide debris inside the wear track
mighthave been critical in glazed layer formation. While the glazed
layeris continuothe wear trcontinuousThe glazedresponsibleperatures
aa plausible617 alloy w(Fig. 9).
It is infewear tracksoxygen conoutside whtion of fresand
subseqhigher oxygeven strongis not evideto be heavil
It is faitemperaturpresent wo750 C. Thethe thicknescales [45,4is
shown byThe poor adthe failure ovated tempappears toalloys, as
inpoorwear rhighly plason the surfaon the othebe responsi750 C as
sutwo alloysthus improvalloys rely oof 20wt% Cr[49]. With aSi and
Al, thous protectThe strain-ito hexagonplane to thereduced we
Wear reat high teX32CrMoV3with a sharmost hot w600 C [52]work
tool sume loss itother handmore wearwear volumgesting thapresent
woature.
Hardnbefor
clus
slideel issistaleaddhestionthe
. Theotheely ms theonsi
.
wled
sler pd forr arehelpK.
nces
Inmaers for467auschlevateiang, Wirol,
rk tooFink, Wear oxidationa new component of wear, Trans. Am.
Soc. Steel 1830) 10261034.. Aoh, J.-C. Chen, On the wear
characteristics of cobalt-based hardfacinger after thermal fatigue
and oxidation, Wear 250 (2001) 611620.. Stott, The role of
oxidation in the wear of metals, Tribol. Int. 31 (1998)71.J. Quinn,
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259273.us in the Inconel 617 alloy and marks the boundary ofack all
around the disc sample, it is revealed as dis-patches inside the
wear track in the Stellite 6 alloy.surfaces in the contact zone
have been reported to befor the relatively lower friction
coefcients at high tem-s they increase the carrying surface [44].
This could beaccount of the low friction coefcient in the
Inconelhere the glazed layer in the wear track is uninterrupted
rred from the increased signal intensities across theof the
Inconel 617 and Stellite 6 disc samples that thecentration is
greater inside the wear tracks than it isere oxidation has occurred
statically (Fig. 10). Genera-h surface and defects due to abrasion
via sliding wearuent reoxidation may be responsible for the
relativelyen levels inside thewear tracks. Oxygen signals becomeer
when crossing the glazed layers. Such a signal prolent in the case
of the hotwork tool steelwhich is believedy oxidised both inside
and outside the wear track.r to conclude from the foregoing that
the high-e wear performance of the three alloys tested in therk is
closely linked with their oxidation behaviour attribological
behaviour is strongly affected by thenature,ss, the adherence, and
the morphology of the oxide6]. The thick surface oxide layer on the
tool steel sampleXRD analysis to consist of Fe3O4 and Fe2O3 (Fig.
11a).herence and limited ductility of these oxides promotef the
oxide scale impairing the resistance towear at ele-eratures [47].
Lack of oxide debris sinterability, whichbe adequate in the case of
Inconel 617 and Stellite 6ferred from Fig. 8c, might have also
contributed to theesistance of the tool steel sample [11]. The
adhesive andtic Cr2O3 lm, identied to be the predominant oxidece of
both Inconel 617 and Stellite 6 samples (Fig. 11b),r hand, has
sustained the abrasion and is claimed toble for the improved wear
resistance of these alloys atggested in [47,48]. The reduced
oxidation rate in thesesuppresses the synergy between oxidation and
wear,ing the resistance to wear at 750 C. High-temperaturen Cr to
form protective scales and require a minimumto develop a continuous
Cr2O3 lm to enjoy protectionCr content only as much as 3wt% and
with hardly anye present hot work tool steel evidently lacks a
continu-ive oxide and cannot take advantage of such
protection.nduced phase transformation from
face-centred-cubical-close-packed structure and alignment of the
basaldirection of sliding, could also be responsible for the
ar of the Stellite 6 alloy [50,51].sistance of the X32CrMoV33
tool steel is impairedmperatures also via loss of mechanical
strength.3 tool steel responded to thermal exposure at 750 Cp
hardness drop (Fig. 12). This is not surprising sinceork tool
steels are known to soften starting around. The substantial
softening in the X32CrMoV33 hotteel is believed to have been
critical in the wear vol-has suffered. Inconel 617 and Stellite 6
alloys, on the, retain their hardness at 750 C and are thus
muchresistant owing to a higher resistance to abrasion. Thee loss
and hot hardness are inversely proportional sug-t the wear
resistance of the three alloys tested in therk is closely linked
with their hardness at this temper-
Fig. 12.samples
4. Con
Thetool sttion re750 Cof an asive acsurvivesurfaceon
therelativsustainbe resp750 C
Ackno
D. IthankeO. Cakfor hisTUBITA
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gements
erformed the ball-on-disc wear tests. Prof. M. Urgen isthe
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High temperature sliding wear behaviour of Inconel 617 and
Stellite 6 alloysIntroductionExperimentalResults and
discussionConclusionsAcknowledgementsReferences