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processes become more strongly temperature dependent, possibly with a transition
in mechanism, such as from cross-slip control to climb control, and the recovery is
now envisaged as being primarily a function of time. A steady state condition is
then more readily achieved, often after quite small strains (*0.01-0.1). We
therefore begin by discussing in a general and largely phenomenological way the
deformation kinetics when time-dependent recovery is important, taking the case
of creep, for simplicity, and generalizing the treatment of Sect. 6.6.4 .
As in Sect. 6.6.4 , we assume that the applied stress is supported primarily by the
mutual dislocation interactions, as represented by the flow stress component s d ;
and that s d tends to increase due to strain hardening during creep. We now assume,
in addition, that s d tends to decrease due to recovery as time progresses, and that
the resultant effect can be written as
Ds d ¼ hc rt
and hence ( 6.34 ) becomes
DE ¼ bDA
ð
hc rt
Þ U
ð 6 : 39 Þ
where c is the plastic strain, t the elapsed time, and the parameters h, r, respec-
tively, the strain-hardening rate and the recovery rate. Both h and r can, in prin-
ciple, be determined empirically, h by carrying out a stress-strain test at a
relatively high strain rate at the conclusion of the creep test and r as set out in Sect.
6.5.3 (Poirier 1985 , p. 105). Using the above expression for Ds d in ( 6.34 ) and
following the same procedure as in deriving ( 6.35a ) the following relation for the
strain is obtained:
h
i
e t r 1
c tot ¼ c inst þ c 0 ln 1 þ ms r
ð 6 : 40a Þ
where c tot and c inst are the total and instantaneous (elastic plus plastic) strains,
respectively, and c 0 ; s and m are given by
kT
hbDA
c 0 ¼
ð 6 : 40b Þ
kT
rbDA
s r ¼
ð 6 : 40c Þ
exp U bDA
m ¼ q 2 bDAm 0
c 0
ð
s hc inst
Þ
1 exp sbDA
kT
ð 6 : 40d Þ
kT
For the case sbDA kT ; ( 6.40d ) reduces to ( 6.35c ) and for the case sbDA
kT (and therefore also sbDA kT), ( 6.40d ) becomes
m ¼ q 2 sb 2
D ð 2 m 0
c 0
exp U þ hc inst bDA
kT
ð 6 : 40e Þ
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