advances in numerical modeling of manufacturing processes
advances in numerical modeling of manufacturing processes
advances in numerical modeling of manufacturing processes
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TRANS. INDIAN INST. MET., VOL. 57, NO. 4, AUGUST 2004<br />
2.2.3 Partial recrystallization <strong>in</strong> a multi-stage<br />
deformation process<br />
Often dur<strong>in</strong>g the roll<strong>in</strong>g process, the time <strong>in</strong> the<br />
<strong>in</strong>terstand is not sufficient for complete<br />
recrystallization to occur. In other words, some<br />
amount <strong>of</strong> stra<strong>in</strong> is reta<strong>in</strong>ed <strong>in</strong> the microstructure<br />
when it enters the next deformation pass. Several<br />
approaches have been proposed to handle partial<br />
recrystallization. One <strong>of</strong> the approaches is to treat<br />
the microstructure as an aggregate. The reta<strong>in</strong>ed stra<strong>in</strong><br />
and the effective gra<strong>in</strong> sizes are determ<strong>in</strong>ed us<strong>in</strong>g the<br />
rule <strong>of</strong> mixtures:<br />
ε<br />
ret<br />
= ε ⋅( 1− X )<br />
(8)<br />
d<br />
eff<br />
( 1−<br />
X ) ⋅ d0<br />
= X ⋅ d +<br />
(9)<br />
rex<br />
where, X is the fraction recrystallized, ε ret<br />
is the<br />
reta<strong>in</strong>ed stra<strong>in</strong>, d<br />
eff is the effective gra<strong>in</strong> size, d<br />
0<br />
is the <strong>in</strong>itial as heated gra<strong>in</strong> size and d rex<br />
is the<br />
recrystallized gra<strong>in</strong> size.<br />
The other approach is to treat the recrystallized and<br />
unrecrystallized fractions <strong>in</strong>dependently (Karhausen<br />
and Kopp 24 ). However, the number <strong>of</strong> fractions to<br />
be handled <strong>in</strong>creases exponentially, which calls for<br />
tremendous amount <strong>of</strong> computer memory and time.<br />
Yanagimoto et al. 25 proposed a variation <strong>of</strong><br />
Karhausen’s model. In this approach, the number <strong>of</strong><br />
fractions <strong>in</strong>creases l<strong>in</strong>early, which requires<br />
considerably less memory. However, as with the rule<br />
<strong>of</strong> mixtures, considerable approximation is <strong>in</strong>volved<br />
and the true behavior <strong>of</strong> the system is not represented.<br />
Here, three hit compression tests were conducted to<br />
determ<strong>in</strong>e the validity <strong>of</strong> the rule <strong>of</strong> mixtures. In the<br />
three hit compression tests, the first <strong>in</strong>ter hit time<br />
was kept deliberately short to cause partial<br />
recrystallization. The second hit was followed by a<br />
third hit with an <strong>in</strong>ter-hit time between the two. The<br />
amount <strong>of</strong> recrystallization <strong>in</strong> the second <strong>in</strong>ter-hit<br />
time was measured us<strong>in</strong>g the same procedure as was<br />
used <strong>in</strong> the double hit compression tests. It was found<br />
that the rule <strong>of</strong> mixtures shows a better correlation<br />
with the measurements for TMS80R and was hence<br />
used <strong>in</strong> the <strong>in</strong>tegrated model.<br />
2.3 Microstructure dependent flow stress model<br />
Flow stress <strong>of</strong> steel at hot roll<strong>in</strong>g temperatures was<br />
found to be strongly dependent on the microstructure,<br />
specifically the austenite gra<strong>in</strong> size <strong>in</strong> addition to<br />
process parameters such as stra<strong>in</strong>, stra<strong>in</strong> rate and<br />
temperature.<br />
f<br />
( ε , & ε , T,<br />
d )<br />
σ = f<br />
(10)<br />
0<br />
A microstructure dependent flow stress model was<br />
developed and <strong>in</strong>tegrated <strong>in</strong>to the FEM module. The<br />
flow stress model is capable <strong>of</strong> model<strong>in</strong>g the<br />
metallurgical phenomena such as stra<strong>in</strong> harden<strong>in</strong>g,<br />
dynamic recovery and recrystallization. Figures 3 and<br />
4 demonstrate the capability <strong>of</strong> the flow stress to<br />
model accurately the work harden<strong>in</strong>g and thermal<br />
s<strong>of</strong>ten<strong>in</strong>g <strong>processes</strong> occurr<strong>in</strong>g dur<strong>in</strong>g plastic<br />
deformation <strong>of</strong> steels under constant stra<strong>in</strong> rate as<br />
well as chang<strong>in</strong>g stra<strong>in</strong> rate conditions. Details about<br />
the microstructure dependent flow stress model can<br />
be found <strong>in</strong> Pauskar et al. 16<br />
2.4 Integrated Model and Validation<br />
The central feature <strong>of</strong> the <strong>in</strong>tegrated system is a three<br />
dimensional f<strong>in</strong>ite element program ROLPAS for<br />
simulat<strong>in</strong>g multi-pass shape roll<strong>in</strong>g. The nonisothermal<br />
deformation analysis <strong>in</strong> ROLPAS is based<br />
on rigid-viscoplastic assumption <strong>of</strong> the material<br />
behavior as described earlier and uses eight-node<br />
isoparametric hexahedral elements. Deformation<br />
with<strong>in</strong> the roll gap is assumed to be k<strong>in</strong>ematically<br />
steady. Such an assumption has been successfully<br />
applied earlier to steady state <strong>processes</strong> such as<br />
extrusion and roll<strong>in</strong>g.<br />
A microstructure evolution module MICON was<br />
developed and <strong>in</strong>tegrated <strong>in</strong>to ROLPAS to enable<br />
model<strong>in</strong>g <strong>of</strong> austenite evolution. MICON uses the<br />
thermomechanical history computed by the FEM<br />
model <strong>in</strong> conjunction with microstructure evolution<br />
models to determ<strong>in</strong>e the evolution <strong>of</strong> austenite dur<strong>in</strong>g<br />
hot roll<strong>in</strong>g. The evolv<strong>in</strong>g austenite was found to<br />
significantly affect the flow stress <strong>of</strong> the material<br />
while the material flow affects recrystallization<br />
k<strong>in</strong>etics. This situation calls for an iterative approach<br />
<strong>in</strong> model<strong>in</strong>g metal flow and austenite evolution. For<br />
the first pass, an <strong>in</strong>itial preheated gra<strong>in</strong> size is <strong>in</strong>put<br />
to the program. After deformation and heat transfer<br />
computations for each pass, the microstructure<br />
evolution module <strong>in</strong> conjunction with the heat transfer<br />
348