控制轧制对高锰高氮奥氏体钢组织与性能的影响

doi:10.12068/j.issn.1005-3026.2025.20240078

摘要/Abstract

摘要：

为提升高锰高氮奥氏体钢的屈服强度，采用SEM、EBSD等表征手段，系统研究了控制轧制工艺对Fe-Mn-Cr-N体系高锰高氮奥氏体钢微观组织演变及力学性能的影响，分析了再结晶区轧制和未再结晶区轧制两种轧制工艺在不同轧制温度下实验钢的组织与性能演变特征.当终轧温度从1 040 ℃下降至973 ℃时，实验钢的平均晶粒尺寸减小，同时出现少量变形组织，其强度、塑性和韧性均随终轧温度降低而略有提高.当终轧温度下降至未再结晶区内的849 ℃时，实验钢内充满具有更高位错密度的变形奥氏体晶粒，屈服强度和抗拉强度均显著提高.未再结晶区的低温轧制可以克服传统高锰奥氏体钢屈服强度不足的局限，获得较好的综合力学性能.

关键词: 控制轧制, 终轧温度, 高锰高氮奥氏体钢, 组织性能, 位错强化

Abstract:

To improve the yield strength of high-manganese and high-nitrogen austenitic steels， characterization methods such as scanning electron microscope （SEM） and electron backscatter diffraction （EBSD） were used， and the influence of the controlled rolling process on the microstructure evolution and mechanical properties of high-manganese and high-nitrogen austenitic steels in the Fe-Mn-Cr-N system was systematically investigated. The evolution characteristics of the microstructure and properties of the experimental steels were analyzed in two rolling processes at different temperatures： rolling in the recrystallization zone and the non-recrystallization zone. When the finish rolling temperature decreased from 1 040 ℃ to 973 ℃， the average grain size of the experimental steels decreased， and a small amount of deformation microstructures appeared. Accordingly， the strength， plasticity， and toughness were slightly improved. When the finish rolling temperature dropped to 849 ℃ in the non-recrystallization zone， the experimental steels were filled with deformed austenite grains with higher dislocation density， and the yield strength and tensile strength increased significantly. Low-temperature rolling in the non-recrystallization zone could overcome the limitations of insufficient yield strength of traditional high-manganese austenitic steels and obtain better comprehensive mechanical properties.

Key words: controlled rolling, finish rolling temperature, high-manganese and high-nitrogen austenitic steel, microstructure and performance, dislocation strengthening

中图分类号:

TG 335.5

张楚恒, 李艳梅, 邓想涛, 王昭东. 控制轧制对高锰高氮奥氏体钢组织与性能的影响[J]. 东北大学学报（自然科学版）, 2025, 46(11): 58-65.

Chu-heng ZHANG, Yan-mei LI, Xiang-tao DENG, Zhao-dong WANG. Influence of Controlled Rolling on Microstructure and Performance of High-Manganese and High-Nitrogen Austenitic Steels[J]. Journal of Northeastern University(Natural Science), 2025, 46(11): 58-65.

图/表 10

表1 实验钢的化学成分(质量分数) (steels (mass fraction) %)

Table 1 Chemical composition of experimental

C	Mn	Si	Cr	Cu	N	Nb
0.01	25.00	0.23	13.5	1.04	0.35	0.08

图1 拉伸试样尺寸（单位：mm）

Fig.1 Tensile specimen’s size(unit:mm)

图 2 终轧温度实验钢的 EBSD 晶体学分析（a）~（c）—终轧温度1 040 ℃；（d）~（f）—终轧温度973 ℃；（g）~（i）—终轧温度849 ℃.

Fig.2 EBSD crystallographic analysis of experimental steels at final rolling temperature

图3 实验钢的局部取向差分布曲线图

Fig.3 Curve showing local misorientation distribution of experimental steels

图4 实验钢的晶粒尺寸及分布统计图（a）—平均晶粒尺寸；（b）—晶粒尺寸分布统计图.

Fig.4 Statistical chart of grain size and distribution of experimental steels

图5 实验钢的拉伸曲线及室温冲击功（a）—工程应力-应变曲线；（b）—室温冲击功.

Fig.5 Tensile curves and room-temperature impact energy of experimental steels

表2 实验钢的力学性能

Table 2 Mechanical properties of experimental steels

终轧温度/℃	屈服强度/MPa	抗拉强度/MPa	延伸率/%	屈强比
1 040	435	744	55.0	0.58
973	452	758	56.7	0.60
849	770	893	35.9	0.86

图6 实验钢加工硬化率曲线（a）—不同终轧温度对比；（b）—终轧温度1 040 ℃；（c）—终轧温度973 ℃；（d）—终轧温度849 ℃.

Fig.6 Strain hardening rate curves of experimental steels

图7 实验钢拉伸试样断口SEM形貌（a）~（c）—终轧温度1 040 ℃；（d）~（f）—终轧温度973 ℃；（g）~（i）—终轧温度849 ℃.

Fig.7 SEM morphologies of tensile fracture surface of experimental steels

图8 实验钢冲击断口的SEM形貌（a）—终轧温度1 040 ℃；（b）—终轧温度973 ℃；（c）—终轧温度849 ℃.

Fig.8 SEM morphologies of impact fracture surface of experimental steels

参考文献 18

[1]	Guo H Y， Wu W T， Tan X， et al. Enhancing mechanical performance of high manganese austenitic steel through deformation at cryogenic temperatures and high strain rates［J］. Materials Characterization， 2025， 228： 115379.
[2]	Wang Y H， Zhang Y B， Godfrey A， et al. Cryogenic toughness in a low-cost austenitic steel［J］. Communications Materials， 2021， 2（1）： 44.
[3]	任家宽. 高锰奥氏体钢极低温强韧化机理研究及新钢种开发［D］. 沈阳：东北大学，2022.
	Ren Jia-kuan. Study on strengthening and toughening mechanism of high manganese austenitic steel at extremely low temperature and development of new steel grades［D］. Shenyang： Northeastern University， 2022.
[4]	Qi X Y， Fang Q W， Wang Z K， et al. Effect of interstitial carbon/nitrogen content on microstructure and tensile deformation behavior of Cr-bearing high-Mn steel［J］. Materials Science and Engineering： A， 2025， 943： 148792.
[5]	Liu Z G， Gao X H， Xiong M， et al. Role of hot rolling procedure and solution treatment process on microstructure， strength and cryogenic toughness of high manganese austenitic steel［J］. Materials Science and Engineering： A， 2021， 807： 140881.
[6]	Sohn S S， Hong S， Lee J， et al. Effects of Mn and Al contents on cryogenic-temperature tensile and Charpy impact properties in four austenitic high-Mn steels［J］. Acta Materialia， 2015， 100： 39-52.
[7]	De Barbieri F， Jorge-Badiola D， Allende R， et al. Effect of Cr content in temperature-dependent mechanical properties and strain hardening of a twinning-induced plasticity steel［J］. Materials Science and Engineering： A， 2024， 889： 145865.
[8]	Lee S M， Park I J， Jung J G， et al. The effect of Si on hydrogen embrittlement of Fe-18Mn-0.6C-xSi twinning-induced plasticity steels［J］. Acta Materialia， 2016， 103： 264-272.
[9]	Liu D， Yang D P， Hou Y， et al. Strain rate effects on mechanical properties， microstructural evolution， and deformation mechanisms of high manganese steels［J］. Journal of Materials Science & Technology， 2025， 237： 219-255.
[10]	Tang C L， Yang J F， Zhang F， et al. Twin-related grain boundary engineering of additively manufactured 316L stainless steel［J］. Acta Materialia， 2025， 301： 121503.
[11]	Liang Z Y， Li Y Z， Huang M X. The respective hardening contributions of dislocations and twins to the flow stress of a twinning-induced plasticity steel［J］. Scripta Materialia， 2016， 112： 28-31.
[12]	Liu C L， Franz R， Dierk R. Finite strain crystal plasticity-phase field modeling of twin， dislocation， and grain boundary interaction in hexagonal materials［J］. Acta Materialia， 2023， 242：118444.
[13]	De Cooman B C， Estrin Y， Kim S K. Twinning-induced plasticity （TWIP） steels［J］. Acta Materialia， 2018， 142： 283-362.
[14]	Kubin L P， Mortensen A. Geometrically necessary dislocations and strain-gradient plasticity： a few critical issues［J］. Scripta Materialia， 2003， 48（2）： 119-125.
[15]	Gao H， Huang Y， Nix W D， et al. Mechanism-based strain gradient plasticity： I. theory［J］. Journal of the Mechanics and Physics of Solids， 1999， 47（6）： 1239-1263.
[16]	Zhu C Y， Harrington T， Gray G T， et al. Dislocation-type evolution in quasi-statically compressed polycrystalline nickel ［J］. Acta Materialia， 2018， 155： 104-116.
[17]	Chen J， Ren J K， Liu Z Y， et al. The essential role of niobium in high manganese austenitic steel for application in liquefied natural gas tanks［J］. Materials Science and Engineering： A， 2020， 772： 138733.
[18]	Bouaziz O， Allain S， Scott C P， et al. High manganese austenitic twinning induced plasticity steels： a review of the microstructure properties relationships［J］. Current Opinion in Solid State and Materials Science， 2011， 15（4）： 141-168.