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Chapter 13
Creep and
Superplasticity
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Creep Strain vs.Time: Constant
Temperature
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Creep Strain vs. Time at Constant
Engineering Stress
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Creep machine with variable lever arms to ensure constant stress on
specimen; note that l2 decreases as the length of the specimen
increases.
Creep Machine
Initial position Length of specimen has increased
from L0 to L1.
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Mukherjee-Bird-Dorn Equation
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Relationship between time to rupture
and temperature at three levels of
engineering stress, a, b, and c,
using LarsonMiller equation (a > b >c).
Larson-Miller Equation
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Master plot for LarsonMiller parameter for S-590 alloy (an
Fe-based alloy) (C= 17).
(From R. M. Goldhoff, Mater.Design Eng., 49 (1959) 93.)
Larson-Miller Parameter
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Relationship between time rupture and temperature at three
levels of stress, a, b, and c, using MansonHaferd
parameter (a > b > c).
Manson-Hafered Parameter
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Relationship between time to rupture and temperature
at three levels of stress, a > b > c, using Sherby
Dorn parameter.
Sherby-Dorn Parameter
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Material Parameters
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Activation energies for creep (stage II) and self-diffusion for a number
of metals.
(Adapted with permission from O. D. Sherby and A. K. Miller, J. Eng. Mater.Technol., 101 (1979) 387.)
Activation Energies for Creep
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Ratio between activation energy for secondary creep and
activation energy for bulk diffusion as a function of temperature.
(Adapted with permission from O. D. Sherby and A. K. Miller, J. Eng. Mater. Technol., 101 (1979) 387.)
Secondary Creep
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Fundamental Creep Mechanism
/G < 10^(-4) Diffusion Creep
Nabarro Herring
Coble Creep
Harper Dorn Creep
2( ) ( )l
N H
D Gb bA
kT d G
=&
3( )( ) ( )c cGb b
AkT b d G
=&
( )l
HD HD
D GbA
kT G
=&
( )l
HD HD
D GbA
kT G
=&
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Flow of vacancies according to (a) NabarroHerring and (b) Coble
mechanisms, resulting in an increase in the length of thespecimen.
Diffusion Creep
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Dislocation climb (a) upwards, under compressive 22
stresses, and (b) downwards, under tensile 22 stresses.
Dislocation Climb
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Different regimes for diffusion creep in alumina; notice that cations
(Al3+) and anions (O2) have different diffusion coefficients, leading to
different regimes of dominance.
(From A. H. Chokshi and T. G. Langdon, Defect and Diffusion Forum, 6669 (1989) 1205.)
Diffusion Creep
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Power relationship between and for AISI 316 stainless steel.
Adapted with permission from S. N. Monteiro and T. L. da Silveira, Metalurgia-ABM, 35 (1979) 327.
Power Law CreepDislocation (Power Law) Creep: 10^(-2) < /G < 10^(-4)
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Dislocation overcoming obstacles by climb, according to Weertman
theory. (a) Overcoming CottrellLomer locks. (b) Overcoming an
obstacle.
Dislocations Overcoming ObstaclesWeertman Mechanism
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Shear stress vs. shear
strain rate in an aluminum (6061)with 30 vol.% SiC particulate
composite in creep.
(From K.-T. Park, E. J. Lavernia, and F. A. Mohamed,
Acta Met. Mater., 38 (1990) 2149.)
Shear Stress and Shear Strain Rate
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Effect of stress and
temperature on deformation
substructure developed inAISI 316 stainless steel in
middle of stage II.
Reprinted with permission from H.-J.
Kestenbach, W. Krause, and
T. L. da Silveira,Acta Met., 26 (1978) 661.)
Dislocation Glide
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(a) Steady-state
grain-boundary sliding with
diffusional accommodations.
(b) Same process as in (a), in an
idealized polycrystal; the dashed
lines show the flow of vacancies.
(Reprinted with permission from
R. Raj and M. F. Ashby, Met. Trans.,
2A (1971) 1113.)
Grain Boundary Sliding
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Grain-boundary sliding assisted by diffusion in AshbyVerralls model.
(Reprinted with permission from M. F. Ashby and R. A. Verrall,Acta Met., 21 (1973) 149.)
Ashby-Verralls Model
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WeertmanAshby map for pure silver, established for a critical
strain rate of 108 s1; it can be seen how the deformation-
mechanism fields are affected by the grain size.
Adapted with permission from M. F. Ashby,Acta Met., 20 (1972) 887.
Weertman-Ashby Map for Pure Silver
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WeertmanAshby map for tungsten,
showing constant strain-rate contours.
(Reprinted with permission from M. F. Ashby,Acta Met., 20
(1972) 887.)
Weertman-Ashby Map for Tungsten
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Weertman-Ashby Map for Al2O3
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.(From W.D. Nix and J. C. Gibeling, in Flow and Fracture at ElevatedTemperatures,
ed, R. Raj (Metals Park, Ohio: ASM, 1985).)
Mechanisms of intergranular nucleation
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Transmission electron micrograph of
Mar M-200; notice the cuboidal
precipitates.
(Courtesy of L. E. Murr.)
Heat-Resistance Materials
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(Reprinted with from C. T. Sims and W. C. Hagel, eds., The
Superalloys (New York: Wiley, 1972), p. 33.)
Microstructural Strengthening Mechanism
in nickel-based superalloys
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Rafting in MAR M-200 monocrystalline superalloy; (a) original
configuration of gamma prime precipitates aligned with threeorthogonal cube axes; (b) creep deformed at 1253 K for 28
hours along the [010] direction, leading to coarsening of
precipitates along loading direction.
(From U. Glatzel, Microstructure and Internal Strains of Undeformed and Creep Deformed Samples of a
Nickel-Based Superalloy,
Habilitation Dissertation,Technische Universitat, Berlin,
1994.)
Rafting
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Stress versus temperatures curves forrupture in
1,000 hours for selected nickel-based
superalloys.
(Reprinted with permission from C. T. Sims and W. C. Hagel,
eds., The Superalloys (New York: Wiley, 1972), p. vii.)
Stress-Rupture (at 1000 hours) vs.
Temperature for Heat Resistant Materials
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Cross-section of a gas turbine showing different parts.
The temperature of gases in combustion chamber reaches 1500 C.
Gas Turbine
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(a) Single crystal
turbine blade developed for
stationary turbine. (Courtesyof U. Glatzel.) (b) Evolution of
maximum temperature in gas
turbines; notice the
significant improvement
made possible by the
introduction of thermalbarrier coatings (TBCs).
(Courtesy of V. Thien, Siemens.)
Turbine Blade
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Springdashpot analogs (a) in series and (b) in parallel.
Creep in Polymers
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(a) Straintime and
(b) stresstime
predictions for
Maxwell and Voigtmodels.
Maxwell and Voigt Models
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Strain response as a function of time for a glassy, viscoelastic
polymer subjected to a constant stress 0. Increasing the
molecular weight or degree of cross-linking tends to promote
secondary bonding between chains and thus make the polymer
more creep resistant.
Viscoelastic Polymer
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(a) A series of creep
compliances vs. time, both on
logarithmic scales, over a range
of temperature. (b) The
individual plots in (a) can be
superposed by horizontal
shifting (along the log-time axis)by an amount log aT, to obtain a
master curve corresponding to a
reference temperature Tgof the
polymer. (c) Shift along the log-
time scale to produce a master
curve.
(Courtesy of W. Knauss.)(d) Experimentally determined
shift factor.
Creep Compliances
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A constant imposed strain 0 results in a drop in stress (t) as a function of time.
Stress Relaxation
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A master curve obtained in the case of stress relaxation, showing the
variation in the reduced modulus as a function of time. Also shown is the
effect of cross-linking and molecular weight.
Effect of Crosslinking on Stress Relaxation
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Metal interconnect line covered by
passivation layer subjected
toelectromigration;
(a) overall scheme;
(b) voids and cracks producedby thermal mismatch and
electromigration;
(c) basic scheme used in Nix
Arzt equation, which assumes
grain-boundary diffusion of
vacancies counterbalancing
electron wind.
(Adapted from W. D. Nix and E. Arzt.
Met. Trans., 23A (1992) 2007.)
Electromigration
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Superplastic tensile deformation in Pb62% Sn eutectic alloy
tested at 415 K and a strain rate of 1.33 104 s1; total strainof 48.5.
(From M. M. I. Ahmed and T. G. Langdon, Met. Trans. A, 8 (1977) 1832.)
Superplasticity
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(a) Schematic representation of plastic deformation in
tension with formation and inhibition of necking. (b)
Engineering-stress engineering-strain curves.
Plastic Deformation
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Strain-rate dependence of (a) stress and (b) strain-rate sensitivity
for MgAl eutectic alloy tested at 350 C (grain size 10 m).
(After D. Lee,Acta. Met., 17 (1969) 1057.)
Strain Rate Dependence
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Tensile fracture strain and stress as a function of strain
rate for Zr22% Al alloy with 2.5-m grain size.
(After F. A. Mohamed, M. M. I. Ahmed, and T. G. Langdon, Met. Trans. A, 8 (1977) 933.)
Fracture
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Effect of strain-rate sensitivity m on maximum tensile
elongation for different alloys (Fe, Mg, Pu, PbSr, Ti, Zn, Zr
based).
(From D. M. R. Taplin, G. L. Dunlop, and T. G. Langdon,Ann. Rev. Mater. Sci., 9 (1979) 151.)
Effect of Strain Rate Sensitivity
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Cavitation in superplasticity formed 7475-T6 aluminum alloy (=
3.5) at 475 C and 5 104 s1. (a) Atmospheric pressure. (b)
Hydrostatic pressure P= 4 MPa. (Courtesy of A. K. Mukherjee.)
Cavitation in Superplasticity
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(a) Effect of grain size on
elongation: (A) Initial
configuration. (B) Large
grains. (C) Fine grains (10 m)
(Reprinted with permission
from N. E. Paton, C. H.
Hamilton, J. Wert, and M.
Mahoney, J. Metal, 34 (1981) No.8, 21.)
(b) Failure strains
increase with superimposed
hydrostatic pressure (from 0 to
5.6 MPa). (Courtesy ofA. K. Mukherjee.)
Effect of Grain Size on Elongation