<strong>3Mn-0.2C</strong>中锰钢形变诱导铁素体动态相变机理

doi:10.11900/0412.1961.2021.00192

金属学报

2022, Vol. 58

Issue (5): 649-659 DOI: 10.11900/0412.1961.2021.00192

研究论文

本期目录 | 过刊浏览

3Mn-0.2C中锰钢形变诱导铁素体动态相变机理

孙毅¹^,², 郑沁园²^,³, 胡宝佳²^,³, 王平¹(

), 郑成武²^,³(

), 李殿中²^,³

^1.东北大学材料电磁过程研究教育部重点实验室沈阳 110819
^2.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
^3.中国科学技术大学材料科学与工程学院沈阳 110016

Mechanism of Dynamic Strain-Induced Ferrite Transformation in a 3Mn-0.2C Medium Mn Steel

SUN Yi¹^,², ZHENG Qinyuan²^,³, HU Baojia²^,³, WANG Ping¹(

), ZHENG Chengwu²^,³(

), LI Dianzhong²^,³

^1.Key Laboratory of Electromagnetic Processing of Materials, Ministry of Education, Northeastern University, Shenyang 110819, China
^2.Shenyang National Laboratory for Materials Science, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
^3.School of Materials Science and Engineering, University of Science and Technology of China, Shenyang 110016, China

引用本文:

孙毅, 郑沁园, 胡宝佳, 王平, 郑成武, 李殿中. 3Mn-0.2C中锰钢形变诱导铁素体动态相变机理[J]. 金属学报, 2022, 58(5): 649-659.
Yi SUN, Qinyuan ZHENG, Baojia HU, Ping WANG, Chengwu ZHENG, Dianzhong LI. Mechanism of Dynamic Strain-Induced Ferrite Transformation in a 3Mn-0.2C Medium Mn Steel[J]. Acta Metall Sin, 2022, 58(5): 649-659.

全文: PDF(5862 KB) HTML

摘要:

利用Gleeble热模拟、SEM、EBSD和EPMA等方法,研究了3Mn-0.2C中锰钢热变形中发生的形变诱导铁素体相变的组织转变行为,分析了中锰钢形变诱导超细晶组织的形成机理及其在热变形后亚动态过程中的组织稳定性。结果表明,3Mn-0.2C中锰钢在α + γ两相区变形时会诱发形变诱导铁素体相变,通过相变形成由超细晶铁素体、细小残余奥氏体和马氏体组成的多相组织。形变诱导铁素体以不饱和形核和有限生长的模式进行相变,这是导致铁素体晶粒超细化的重要机理。同时,在超细晶铁素体晶界及三叉晶界处形成的细小富Mn残余奥氏体使形变诱导相变组织具有优异的组织稳定性。

关键词 ：热变形, 超细晶铁素体, Mn配分, 形变诱导铁素体相变, 中锰钢

Abstract：

Medium Mn steels (MMSs) have Mn contents of 3%-12% (mass fraction), and have been energetically investigated as the most promising candidates of the third-generation advanced high-strength steel. Their phase transformations and microstructures during various heat treatments and thermomechanical processes have received wide attention with the purpose to achieve an optimal balance of cost-efficient alloying compositions and mechanical properties. The aim of this work is to investigate the microstructural behavior of deformation-induced ferrite transformation (DIFT), starting from austenite, which occurs in MMS. Then, improved understandings of the formation of ultrafine ferrite via the DIFT and conservation of this microstructure during the post-deformation period can be obtained. For this purpose, a 3Mn-0.2C MMS with lower contents of alloying elements was selected. Microstructures and alloying element distributions of the thermomechanically processed samples were analyzed via EBSD and EPMA. The results showed that the DIFT occurred in the thermomechanically processed 3Mn-0.2C MMS in the α + γ region. Characteristic multiphase microstructures consisting isolated martensite and fine-grained equiaxed ferrite concomitant with fine islands of retained austenite dispersed between ferrite grains can be obtained. During the DIFT, the enhanced nucleation of ferrite at α/γ interfaces can not only increase the ferrite nucleation density but also facilitate extensive impingement among the neighboring grains. Formation of ultrafine ferrite via the DIFT in MMS can be interpreted in terms of unsaturated nucleation and limited growth. In addition, partitioning of Mn between the ultrafine ferrite and austenite is accelerated during the DIFT such that a large number of Mn-enriched fine islands of austenite are left untransformed at the α/α grain boundaries or at triple junctions. These islands of austenite are considered to play critical roles not only for obtaining retained austenite at room temperature but also for conserving the ultrafine microstructure of the DIFT during the post-deformation processing.

Key words： hot deformation ultra-fine grained ferrite Mn partitioning deformation induced ferrite transformation medium Mn steel

收稿日期: 2021-05-07

ZTFLH:

TG142.1

基金资助:国家自然科学基金项目(52071322);国家自然科学基金项目(51771192);国家自然科学基金项目(U1708252)

作者简介: 孙毅,男,1995年生,硕士生

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https://www.ams.org.cn/CN/10.11900/0412.1961.2021.00192 或 https://www.ams.org.cn/CN/Y2022/V58/I5/649

图1 3Mn-0.2C中锰钢(MMS)形变诱导铁素体相变实验及等温铁素体相变实验的工艺示意图

图2 3Mn-0.2C MMS在660℃、0.001 s-1条件下变形的真应力-真应变曲线及不同应变时微观组织的EBSD像

图3 3Mn-0.2C MMS在T = 660℃保温1800 s后和相同温度下以应变速率 ε˙ = 0.001 s-1变形至应变ε = 0.51的SEM像

图4 3Mn-0.2C MMS在T = 660℃、 ε˙ = 0.001 s-1条件下变形至不同应变时微观组织的EBSD像

图5 3Mn-0.2C MMS在T = 660℃、 ε˙ = 0.001 s-1条件下变形至ε = 0.92时的SEM像及合金元素分布

图6 3Mn-0.2C MMS在T = 660℃、 ε˙ = 0.001 s-1下变形至ε = 0.92时的微观组织与变形后在相同温度保温1000 s后微观组织的EBSD像

图7 3Mn-0.2C MMS在T = 660℃、 ε˙ = 0.001 s-1下变形至ε = 0.92及变形后在相同温度保温1000 s后的SEM像及Mn元素分布

图8 3Mn-0.2C MMS在T = 660℃下以不同应变速率变形至ε = 0.92时微观组织的EBSD像

图9 3Mn-0.2C MMS在T = 660℃以不同应变速率变形至ε = 0.92时的SEM像及C、Mn元素的分布

图10 中锰钢中形变诱导铁素体相变的微观组织演变示意图

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