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Chinese Journal of Materials Research  2014, Vol. 28 Issue (3): 211-219    DOI: 10.11901/1005.3093.2013.841
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Deformation Behavior and Microstructure Evolution of GH4169 Alloy during the Delta Process
Haiyan ZHANG1,**(),Shihong ZHANG2,Ming CHENG2,Zhong ZHAO1
1. School of Mechanical Engineering, Ningbo University of Technology, Ningbo 315016
2. Institude of Metal Research, Chinese Academy of Sciences, Shenyang 110016
Cite this article: 

Haiyan ZHANG,Shihong ZHANG,Ming CHENG,Zhong ZHAO. Deformation Behavior and Microstructure Evolution of GH4169 Alloy during the Delta Process. Chinese Journal of Materials Research, 2014, 28(3): 211-219.

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Abstract  

For the delta process (DP) of GH4169 high temperature alloy, the effect of d phase content on its hot deformation behavior and evolution of microstructures was studied systematically by isothermal compression test with a strain rate range 0.005-0.1 s-1 at temperature range 950-1010℃. The results indicated that the true stress–true strain curves for GH4169 alloys with different initial d phase contents of 0, 3.65% and 8.14% may be characterized with the feature of single peak curves, and the constitutive equation could be all expressed by a hyperbolic-sine Arrhenius-type equation. The corresponding activation energies of deformation were 441.3, 445.8 and 487.7 kJ/mol, respectively. The main soft mechanisms for GH4169 alloys with different initial d phase contents during hot working were all dynamic recrystallization (DRX). As the increase of δ phase content, the critical strain and grain size of DRX decreased, and the fraction of DRX increased. The DRX nucleation for the solution treated alloy might mainly rely on the bulging of original grain boundaries, while the boundaries between the d phase and matrix were the nucleation sites for DRX in the pre-precipitated GH4169 alloys. Thus, the existence of d phase can stimulate the occurrence of DRX.

Key words:  metallic materials      GH4169 alloy      delta process      δ phase      deformation behavior      microstructure     
Received:  11 November 2013     
Fund: *Supported by Natural Science Foundation of Zhejiang Province No. LQ12E05001 and Natural Science Foundation of Ningbo No.2011A610157.

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https://www.cjmr.org/EN/10.11901/1005.3093.2013.841     OR     https://www.cjmr.org/EN/Y2014/V28/I3/211

Fig.1  OM images of GH4169 for compression tests (a) No.1#, (b) No.2#, (c) No.3#
Fig.2  True stress–true strain curves for GH4169 deformed at 950℃ under various strain rates (a) No.1#, (b) No.2#, (c) No.3#
Fig.3  ln[sinh(ασp)] vs. 1/T for GH4169 during hot compression (a) No.1#, (b) No.2#, (c) No.3#
Fig.4  OM images of GH4169 deformed at 980℃, 0.05 s-1 (a) No.1#, (b) No.2#, (c) No.3#
Fig.5  Peak strain for GH4169 deformed under various deformation conditions
Fig.6  Recrystallization grain size for GH4169 deformed under various deformation conditions
Fig.7  Recrystallization fraction for GH4169 deformed under various deformation conditions
Fig.8  Curves of lnε0.5 vs. ln Z(a) and ln(-ln(1- X)/0.693) vs. ln((ε-εc)/ε0.5) (b) for GH4169 during hot compression
Alloy No. δ phase content /% Critical strain Recrystallized grain size/m Recrystallization fraction
1# 0 ε c = 0.83 ε p
ε p = 4.2 × 10 - 3 Z 0.0990
d= 1.2758 × 10 5 Z - 0.2609 ε 0.5 = 1.3689 × 10 - 4 Z 0.2296
X= 1 - e x p ( - 0.693 × ( ε- ε c ε 0.5 ) 1.69 )
2# 3.65 ε c = 0.83 ε p
ε p = 9.12 × 10 - 3 Z 0.0697
d= 1.5628 × 10 5 Z - 0.2654 ε 0.5 = 8.1051 × 10 - 4 Z 0.1778
X= 1 - e x p ( - 0.693 × ( ε- ε c ε 0.5 ) 2.05 )
3# 8.14 ε c = 0.83 ε p
ε p = 5.899 × 10 - 5 Z 0.1711
d= 3.9796 × 10 5 Z - 0.2649 ε 0.5 = 5.37 × 10 - 3 Z 0.1135
X= 1 - e x p ( - 0.693 × ( ε- ε c ε 0.5 ) 2.43 )
Table 1  Dynamic recrystallization molds for GH4169
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