珠光体-奥氏体相变中扩散通道的相场法研究

doi:10.11900/0412.1961.2021.00306

金属学报

2023, Vol. 59

Issue (10): 1376-1388 DOI: 10.11900/0412.1961.2021.00306

研究论文

本期目录 | 过刊浏览

珠光体-奥氏体相变中扩散通道的相场法研究

李赛¹, 杨泽南², 张弛¹, 杨志刚¹(

)

^1.清华大学材料学院北京 100084
^2.中国航发北京航空材料研究院先进高温结构材料重点实验室北京 100095

Phase Field Study of the Diffusional Paths in Pearlite-Austenite Transformation

LI Sai¹, YANG Zenan², ZHANG Chi¹, YANG Zhigang¹(

)

^1.School of Materials Science and Engineering, Tsinghua University, Beijing 100084, China
^2.Science and Technology on Advanced High Temperature Structural Materials Laboratory, AECC Beijing Institute of Aeronautical Materials, Beijing 100095, China

引用本文:

李赛, 杨泽南, 张弛, 杨志刚. 珠光体-奥氏体相变中扩散通道的相场法研究[J]. 金属学报, 2023, 59(10): 1376-1388.
Sai LI, Zenan YANG, Chi ZHANG, Zhigang YANG. Phase Field Study of the Diffusional Paths in Pearlite-Austenite Transformation[J]. Acta Metall Sin, 2023, 59(10): 1376-1388.

全文: PDF(2572 KB) HTML

摘要:

通过实验方法和基于MICRESS的相场模型，对Fe-0.6%C-2%Mn (质量分数)合金在720和740℃等温时的珠光体-奥氏体相变进行研究。实验结果表明，由动力学曲线可粗略估测出奥氏体/珠光体界面迁移速率，并通过Mn在新生奥氏体中的分布，验证奥氏体相变模式在720和740℃等温时分别为间隙型合金元素C的扩散控制(PLE)模式和置换型合金元素的扩散控制(NPLE)模式。利用相场模拟研究γ、α和界面扩散通道的引入对PLE和NPLE模式下奥氏体/珠光体界面迁移速率的影响，其中NPLE模式下C元素的主要扩散通道可能为奥氏体和铁素体；在PLE模式下，Mn主要通过相界面进行扩散，但相较于奥氏体扩散通道，铁素体扩散通道对相界面迁移产生更大贡献，因此在热动力学分析中不可将其忽略，这与对PLE模式分析的传统认知有所差异。

关键词 ：珠光体, 奥氏体化, 相场模拟, 相变动力学, 元素扩散

Abstract：

In the development of advanced steel, accurate and detailed knowledge about the kinetics of phase transformations and microstructure formation is critical. The critical issue in pearlite-austenite transformation is the consideration of diffusional paths of the alloy element. Simulation has been an available method to study the diffusion of alloy elements and the migration rate of the phase boundary in the complex morphological evolution of austenite growth. The isothermal pearlite-austenite transformations at 720 and 740^oC in Fe-0.6%C-2%Mn (mass fraction) alloy were studied by phase-field methods based on MICRESS. At different temperatures, the effects of diffusional paths on the austenite transformation were discussed. To achieve a semiquantitative verification of the simulated results, the migration rates of the austenite/pearlite boundary at 720 and 740^oC were estimated from the experimental kinetics curves by fitting the JMA equation. By measuring the Mn profile in austenite, the modes of the austenization at 720 and 740^oC can be verified as partitioned local equilibrium (PLE) and non-partitioned local equilibrium (NPLE) modes. The heterogeneous distribution of Mn in austenite at 740^oC can be observed with STEM-EDS. However, the homogenous distribution of Mn can be found near the pearlite/austenite boundary in austenite at 720^oC. The cases considering the γ, α, and interface-diffusional paths were simulated by phase-field methods to compare with the migration rates of the austenite/pearlite boundary. Because carbon is an interstitial element in steel and has an interstitial diffusional mechanism, it can be speculated reasonably that the diffusion of C mainly proceeded in austenite and ferrite through the considerations of the atom-size of carbon and the experimental results. Phase-field methods were used to study Mn diffusion in the lamellar pearlite-austenite transformation. With the analysis of the experimental estimations, the interface-diffusional path was observed as the dominant path for the Mn diffusion. It is because the Mn atoms have greater diffusivity in interfaces than in γ or α-diffusional paths. Furthermore, the diffusional activation energy is closely related to the diffusivity of Mn at the interface. Moreover, compared with the γ-diffusional path, the diffusional flux of Mn in ferrite is much larger than that in austenite. Thus, it can be concluded that the contribution of the α-diffusional path to the migration rate of the pearlite/austenite boundary is larger than that of the γ-diffusional path. As a result, considering the α-diffusional path in the thermodynamics analysis under NPLE mode makes more sense. However, ignoring the interface- and α-diffusional path, which is different from the traditional cognition in PLE mode, will result in a magnitude error for the thermodynamics analysis.

Key words： pearlite austenization phase field simulation kinetics of phase transformation element diffusion

收稿日期: 2021-07-27

ZTFLH:

TG113.1

基金资助:国家自然科学基金项目(51771100)

通讯作者: 杨志刚，zgyang@tsinghua.edu.cn，主要从事金属材料研究

Corresponding author: YANG Zhigang, professor, Tel: (010)62795031, E-mail: zgyang@tsinghua.edu.cn

作者简介: 李赛，男，1994年生，博士生

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表1 模拟编号及所对应的模拟条件

Physical quantity	Item	Value	Unit
Interface energy	γ/α, γ/θ, α/θ	1.5 × 10^-5	J·cm^-2
Interface mobility	γ/α, γ/θ	1.5	cm⁴·J^-1·s^-1
	α/θ	1	cm⁴·J^-1·s^-1
Frequency factor $D 0$	C in γ	0.1996	cm²·s^-1
	C in α	0.419	cm²·s^-1
	C in interface	0.1996	cm²·s^-1
	Mn in γ	0.1501	cm²·s^-1
	Mn in α	6.7119 × 10³	cm²·s^-1
	Mn in interface	0.1501	cm²·s^-1
Activity energy Q	C in γ	1.390 × 10⁵	J·mol^-1
	C in α	1.086 × 10⁵	J·mol^-1
	C in interface	0.97 × 10⁵	J·mol^-1
	Mn in γ	2.602 × 10⁵	J·mol^-1
	Mn in α	3.062 × 10⁵	J·mol^-1
	Mn in interface	1.55 × 10⁵	J·mol^-1
Thickness of the diffusional interface		0.5	nm

表2 本模拟涉及物理量及其取值[26,36]

图1 高温激光共聚焦显微镜观察下样品在720和740℃等温至完全奥氏体化的显微组织

图2 初始珠光体在720和740℃等温时的奥氏体相变动力学曲线

图3 初始珠光体在720℃等温60 s后的显微组织及Mn浓度分布

图4 初始珠光体在740℃等温20 s后的显微组织及Mn浓度分布

图5 等温温度为740℃，扩散通道为γ + α + interface时，珠光体-奥氏体相变组织形貌演化

图6 等温温度为720℃时，珠光体-奥氏体相变组织形貌演化

图7 初始珠光体在740℃等温0.004 s时的浓度分布

图8 初始珠光体在720℃等温3.81 s时的浓度分布

图9 不同模拟条件下奥氏体/珠光体界面迁移速率

图10 考虑γ + α扩散通道时，奥氏体/珠光体界面前沿合金元素浓度分布

图11 合金元素在奥氏体和铁素体中的扩散通量分布

图12 奥氏体/珠光体界面迁移速率随界面扩散激活能(Qint)的变化趋势

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