Forgeabilité des aciers inoxydables austéno-ferritiques
Forgeabilité des aciers inoxydables austéno-ferritiques
Forgeabilité des aciers inoxydables austéno-ferritiques
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tel-00672279, version 1 - 21 Feb 2012<br />
Chapter III. HOT CRACKING RESISTANCE 65<br />
III.3.3 Conclusions<br />
� In this part, the EWF concept was applied at high temperature to different gra<strong>des</strong> of duplex<br />
stainless steels in the as-cast conditions. The results have shown that this method is a discri-<br />
minating tool to characterize the hot tearing resistance of such materials.<br />
� At 1050°C, the grade D1 is two times more resistant to crack propagation than the grade D2.<br />
� At 1200°C, the grade D1 remains more ductile than the grade D2 but the difference in term of<br />
essential specific work of fracture is not significant considering the dispersion of the results.<br />
� Fracture observations and damage quantification match very well with the EWF results.<br />
� Hardness characterizations have permitted to highlight the softening mechanisms involved or<br />
not in each phase: dynamic recovery in the ferrite and no sign of recrystallization but a high<br />
dislocation density in the austenite. This last comment suggests the occurrence of stress and<br />
strain partitioning between ferrite and austenite at high temperature with a more significant ef-<br />
fect in the D2-grade.<br />
� The dispersion of the results is significant, attributed to the microstructure heterogeneity<br />
through the slab thickness: phase ratio and austenite lath size. This last comment suggests<br />
that better results, i.e. with less scattered and more accurate values of the essential specific<br />
work of fracture, could be obtained if homogeneous microstructures are considered.<br />
III.4 Generation of model microstructures<br />
The goal is to develop homogeneous microstructures of either the lath (Widmanstätten microstructure:<br />
‘W’) or the equiaxed γ-austenite (equiaxed microstructure: ‘E’) in a δ-ferrite matrix which is stable at<br />
1050°C, which is thus the temperature selected to measure the hot ductility. This effort to engineer<br />
microstructures must result in (1) a reduction of the dispersion, hence improving the accuracy of the<br />
results and (2) a more accurate determination of the influence of phase morphology on the hot worka-<br />
bility comparing two different austenite morphologies with the same phase ratio. This last point has to<br />
be emphasized because, as pointed out in the bibliographical review (Chapter II), the phase ratio can<br />
significantly affect the hot ductility of duplex stainless steels.<br />
Particular attention is paid to microstructural evolutions leading to different austenite morphologies<br />
starting from the same metallurgical state. In depth understanding of the nucleation and growth during<br />
the δ → γ phase transformation allows the identification of the appropriate heat treatments. Some<br />
details concerning the different heat treatments are given for the D2 grade. For the alloy D1, as the<br />
results are very close to those of the D2 grade, only the resulting microstructures obtained with the<br />
appropriate heat treatments are presented.