Austenite/Ferrite Interface Migration and Alloying Elements Partitioning: An Overview
Hao CHEN, Congyu ZHANG(), Jianing ZHU, Zenan YANG, Ran DING, Chi ZHANG, Zhigang YANG
The Key Laboratory of Advanced Materials of Ministry of Education, School of Materials Science and Engineering, Tsinghua University, Beijing 100084, China
Cite this article:
Hao CHEN, Congyu ZHANG, Jianing ZHU, Zenan YANG, Ran DING, Chi ZHANG, Zhigang YANG. Austenite/Ferrite Interface Migration and Alloying Elements Partitioning: An Overview. Acta Metall Sin, 2018, 54(2): 217-227.
Phase transformation is one of the most effective methods to tailor microstructure of steels. In order to develop high performance steels, microstructure has to be precisely tuned, which requires a deep understanding of phase transformation. The austenite to ferrite transformation in steels has been of great interest for several decades due to its considerable importance in the processing of modern high performance steels, and it has been investigated from various aspects. Mechanism of interface migration and alloying elements partitioning during the austenite to ferrite transformation was regarded as one of the most significant and challenging topics in the field. This paper briefly summarized the recent progress in the understanding of this topic from both theoretical and experimental perspectives, and would also provide discussions and outlook of the unresolved issues.
Fund: Supported by National Key Research and Development Program of China (No.2016YFB0300104) and National Natural Science Foundation of China (Nos.51501099 and 51471094)
Fig.1 Fe-C-M ternary alloy under paraequilibrium (PE) condition(a) isothermal section(b) alloying element profile at the α/γ interface(c) C profile at the α/γ interface. Here, XC is the mole fraction of C and YM is the site fraction of alloying element (YM=XM/(1- XC), XM is the mole fraction of alloying element)
Fig.2 Fe-C-M ternary alloy under local equilibrium (LE) condition(a) isothermal section in partition local equilib- rium (PLE) mode(b) alloying element profile at the α/γ interface in PLE mode(c) C profile at the α/γ interface in PLE mode(d) isothermal section in negligible partition local equilibrium (NPLE) mode(e) alloying element profile at the α/γ interface in NPLE mode(f) C profile at the α/γ interface in NPLE mode
Fig.3 Deviations of Fs and As from T0 upon cooling and heating in the Fe-Ni, Fe-Mn and Fe-Co alloys as a function of the solute concentration[74] (Fs—starting temperature of austenite-ferrite transformation, As—starting temperature of ferrite-austenite transformation, T0—temperature at which the free energies of new phase and parent phase are equal)
Fig.4 Derived interface mobility (Mint) as a function of temperature[74]
Fig.5 Dilation as a function of temperature during cyclic experiments (a) and α/γ interface position as a function of temperature simulated under both local equilibrium and paraequilibrium conditions between 885 and 860 ℃ in Fe-0.17Mn-0.023C (mass fraction, %) alloy (b)[101]
Fig.6 Dilations as a function of temperature during the γ-α cyclic phase transformations with 6 temperature cycles between 842 and 785 ℃ in a Fe-0.49Mn-0.1C (mass fraction, %) alloy (a) and simulated residual Mn spikes in austenite after cyclic phase transformations with 1, 2 and 6 temperature cycles (b)[104]
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