中锰钢奥氏体中化学界面变形行为的晶体塑性研究

doi:10.11900/0412.1961.2023.00004

金属学报

2025, Vol. 61

Issue (2): 349-360 DOI: 10.11900/0412.1961.2023.00004

研究论文

本期目录 | 过刊浏览

中锰钢奥氏体中化学界面变形行为的晶体塑性研究

贾春妮¹, 刘腾远¹^,², 郑成武¹(

), 王培¹, 李殿中¹(

)

1 中国科学院金属研究所沈阳材料科学国家研究中心沈阳 110016
2 中国科学技术大学材料科学与工程学院沈阳 110016

Micro-Deformation Behavior of Austenite Containing Chemical Boundary in a Medium Mn Steel： A Crystal Plasticity Modeling

JIA Chunni¹, LIU Tengyuan¹^,², ZHENG Chengwu¹(

), WANG Pei¹, LI Dianzhong¹(

)

1 Shenyang National Laboratory for Materials Science, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
2 School of Materials Science and Engineering, University of Science and Technology of China, Shenyang 110016, China

引用本文:

贾春妮, 刘腾远, 郑成武, 王培, 李殿中. 中锰钢奥氏体中化学界面变形行为的晶体塑性研究[J]. 金属学报, 2025, 61(2): 349-360.
Chunni JIA, Tengyuan LIU, Chengwu ZHENG, Pei WANG, Dianzhong LI. Micro-Deformation Behavior of Austenite Containing Chemical Boundary in a Medium Mn Steel： A Crystal Plasticity Modeling[J]. Acta Metall Sin, 2025, 61(2): 349-360.

全文: PDF(1625 KB) HTML

摘要:

针对中锰钢奥氏体中形成的Mn化学界面，基于晶体塑性理论框架，建立了考虑位错密度演化及形变诱导相变的晶体塑性模型，研究了单一奥氏体晶粒内部存在化学界面情况下的微观变形行为，获得了奥氏体晶粒内部应力、应变及位错密度的分布，以及变形过程中形变诱导相变分数的演化。结果显示，奥氏体中化学界面的存在不仅能引起晶粒内部的应力与应变产生微区配分，即富Mn侧奥氏体承载更多的应力，贫Mn侧奥氏体承载更多的应变，而且会使同一个奥氏体晶粒内部各处的机械稳定性呈现差异性分布，使奥氏体在变形过程中渐次地发生相变诱导塑性(TRIP)效应，从而提高材料的强度和塑性。

关键词 ：中锰钢, 奥氏体, 化学界面, 形变诱导马氏体相变, 晶体塑性

Abstract：

Chemical boundaries (CBs) delineate two areas within a continuous lattice that have same structures but exhibit a sharp chemical discontinuity. CBs can be seen as a unique planar defect that is distinct in certain aspects from traditional physical interfaces such as phase boundaries and grain boundaries (GBs). Recently, GBs have been established within the austenite of medium Mn steels; they have been proven to substantially enhance the stability of austenite. This allows austenite to be easily retained at room temperature and offers additional possibilities for managing its mechanical stability. In this study, a crystal plasticity modeling was performed to simulate the deformation behavior of austenite containing a CB. First, an extended dislocation-based crystal plastic model that incorporates the deformation-induced martensitic transformation and stacking fault energy was developed. The inverse Nishiyama-Wassermann (N-W) relation was used to accurately describe the orientation relationship between austenite and newly formed martensite. The Mn content on both sides of the CB is taken as a state variable to calculate the stacking fault energy. This leads to varying responses in the deformation-induced martensitic transformation and dislocation slip within a single austenite grain. Results reveal a strain incompatibility between Mn-rich and Mn-poor austenite that causes a geometrically necessary dislocation to accumulate near the CB. Furthermore, the deformation-induced martensitic transformation on both sides of the CB behaves differently, leading to a “spectral” distribution of mechanical stability within a single austenite grain. This heterogeneity in the mechanical stability of austenite is highly beneficial. It allows a gradual deformation-induced phase transformation throughout the entire deformation process, which is crucial for enhancing the strength and plasticity of transformation induced plasticity (TRIP)-aided steels simultaneously.

Key words： medium Mn steel austenite chemical boundary deformation-induced martensite transformation crystal plasticity

收稿日期: 2022-12-30

ZTFLH:

TG142

基金资助:国家自然科学基金项目(52301181);国家自然科学基金项目(52071322)

通讯作者: 郑成武，cwzheng@imr.ac.cn，主要从事先进钢铁微观组织与转变机制研究；
李殿中，dzli@imr.ac.cn，主要从事特殊钢与大构件制备研究

Corresponding author: ZHENG Chengwu, professor, Tel: (024)23971973, E-mail: cwzheng@imr.ac.cn;
LI Dianzhong, professor, Tel: (024)23971281, E-mail: dzli@imr.ac.cn

作者简介: 贾春妮，女，1994年生，博士

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图1 晶体塑性模型中变形梯度乘法分解的示意图

α	$M s = m s α ⊗ n s α$	α	$M s = m s α ⊗ n s α$
1	$01 1 ¯ ⊗ 111 / 6$	7	$011 ⊗ 1 1 ¯ 1 / 6$
2	$10 1 ¯ ⊗ 111 / 6$	8	$10 1 ¯ ⊗ 1 1 ¯ 1 / 6$
3	$1 1 ¯ 0 ⊗ 111 / 6$	9	$110 ⊗ 1 1 ¯ 1 / 6$
4	$01 1 ¯ ⊗ 1 ¯ 11 / 6$	10	$011 ⊗ 11 1 ¯ / 6$
5	$101 ⊗ 1 ¯ 11 / 6$	11	$101 ⊗ 11 1 ¯ / 6$
6	$110 ⊗ 1 ¯ 11 / 6$	12	$1 1 ¯ 0 ⊗ 11 1 ¯ / 6$

表1 fcc结构材料的滑移系

$β t r$	x_tr	y_tr	z_tr	r_tr	θ_tr
1	[100]	[010]	[001]	[010]	+10.26°
2	[100]	[010]	[001]	[010]	-10.26°
3	[100]	[010]	[001]	[001]	+10.26°
4	[100]	[010]	[001]	[001]	-10.26°
5	[010]	[100]	[001]	[100]	+10.26°
6	[010]	[100]	[001]	[100]	-10.26°
7	[010]	[100]	[001]	[001]	+10.26°
8	[010]	[100]	[001]	[001]	-10.26°
9	[001]	[100]	[010]	[100]	+10.26°
10	[001]	[100]	[010]	[100]	-10.26°
11	[001]	[100]	[010]	[010]	+10.26°
12	[001]	[100]	[010]	[010]	-10.26°

表2 反N-W关系定义的12个形变诱导马氏体相变的等效相变系

δ α	1	2	3	4	5	6	7	8	9	10	11	12
1	0	$- 3 / 2$	$- 3 / 2$	0	0	0	0	0	0	0	0	0
2	$3 / 2$	0	$- 3 / 2$	0	0	0	0	0	0	0	0	0
3	$3 / 2$	$3 / 2$	0	0	0	0	0	0	0	0	0	0
4	0	0	0	0	$- 3 / 2$	$- 3 / 2$	0	0	0	0	0	0
5	0	0	0	$3 / 2$	0	$3 / 2$	0	0	0	0	0	0
6	0	0	0	$3 / 2$	$- 3 / 2$	0	0	0	0	0	0	0
7	0	0	0	0	0	0	0	$- 3 / 2$	$- 3 / 2$	0	0	0
8	0	0	0	0	0	0	$3 / 2$	0	$3 / 2$	0	0	0
9	0	0	0	0	0	0	$3 / 2$	$- 3 / 2$	0	0	0	0
10	0	0	0	0	0	0	0	0	0	0	$3 / 2$	$3 / 2$
11	0	0	0	0	0	0	0	0	0	$- 3 / 2$	0	$3 / 2$
12	0	0	0	0	0	0	0	0	0	$- 3 / 2$	$- 3 / 2$	0

表3 fcc滑移系到层错带系的滑移量投影矩阵

$δ$	$M t w = m t w δ ⊗ n t w δ$	α	$M t w = m t w δ ⊗ n t w δ$
1	$2 ¯ 11 ⊗ 111 / 6$	7	$2 ¯ 1 ¯ 1 ⊗ 1 1 ¯ 1 / 6$
2	$1 ¯ 2 1 ¯ ⊗ 111 / 6$	8	$1 ¯ 12 ⊗ 1 1 ¯ 1 / 6$
3	$11 2 ¯ ⊗ 111 / 6$	9	$2 1 ¯ 1 ⊗ 1 1 ¯ 1 / 6$
4	$2 ¯ 1 ¯ 1 ¯ ⊗ 1 ¯ 11 / 6$	10	$1 2 ¯ 1 ¯ ⊗ 11 1 ¯ / 6$
5	$12 1 ¯ ⊗ 1 ¯ 11 / 6$	11	$111 ⊗ 11 1 ¯ / 6$
6	$1 ¯ 1 2 ¯ ⊗ 1 ¯ 11 / 6$	12	$1 ¯ 1 ¯ 2 ¯ ⊗ 11 1 ¯ / 6$

表4 fcc晶体的层错带系

图2 变形梯度及其内部相关变量求解过程的示意图

图3 奥氏体中Mn化学界面微结构的几何模型

图4 奥氏体内部化学界面附近的微区应变演化

图5 奥氏体内部化学界面附近的微区应力演化

表5 奥氏体内部Mn化学界面两侧的微区应力及应变差统计值

图6 应变为0.025时沿图4b和5b中L1-L1'和L2-L2'的微区应力和应变分布情况

图7 应变为0.1时计算所得化学界面附件的位错密度分布

图8 应变为0.05时形变诱导马氏体体积分数分布情况和变形过程中奥氏体内化学界面两侧马氏体相变动力学

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