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摘要: 随着汽车保有量的提高，能源消耗和环境问题对汽车用钢提出了轻量化的要求。目前正在发展的第三代汽车用钢的研究思路是将加入轻量元素以“轻”和增强增塑以“薄”相结合。Fe−Mn−Al−C系中锰钢作为第三代汽车用钢的主要组成部分，是当今的研究热点之一。本文总结了近些年国内外Fe−Mn−Al−C系中锰钢的研究文献，从生产成本、力学性能等方面介绍了Fe−Mn−Al−C系中锰钢的优势。从成分设计、工艺设计、组织特征、变形及断裂机制等多个方面出发，对文献进行分析，总结出了合金成分、工艺路线和组织特征对性能的影响规律。阐述了奥氏体层错能及其稳定性对中锰钢变形机制，尤其是相变诱导塑性（TRIP效应）的影响规律。最后对目前Fe−Mn−Al−C系中锰钢研究过程中存在的争议问题进行了总结，展望了未来的发展趋势，以期为中锰钢的后续研究和实际生产提供参考。Abstract: As vehicle ownership increases, the trend lightweight design puts energy consumption and environmental concerns on automotive steel. The research concept of the third generation of automotive steel currently under development is to combine the addition of lightweight elements with “light” and improve plasticization with “thin”. Some of the research hotspots are Fe−Mn−Al−C medium Mn steels as the main component of the third generation of automotive steel. This paper summarized the research literature of Fe−Mn−Al−C steels in recent years in different countries, and discussed the advantages of Fe−Mn−Al−C medium Mn steels in terms of production cost and mechanical properties; the mechanical properties of that is not worse or even better than the second generation of advanced high-strength automotive steel such as TWIP steel can be obtained under the premise of cost savings. The literature was reviewed from the aspects of composition design, process design, microstructure characteristics, deformation and fracture mechanism, and the effect on the efficiency of chemical composition, process route, and microstructure on performance was summarized. It proposed a reasonable range of chemical elements especially Mn and Al, and compared the focus of the two different process routes (Intercritical annealing and quenching + Tempering). The deformation mechanism of medium Mn steel, especially transformation-induced plasticity (TRIP) effect, and the stacking fault energy and austenite stability were identified, in particular, the factors affecting the austenite stability such as grains size, grain morphology and chemical elements were described, and the three-stage work hardening behavior that often occurs in Fe−Mn−Al−C steels was explained. Furthermore, the literature proposed suggestions on regulating the organization of Fe−Mn−Al−C steels by studying the fracture mechanism of materials. Typically the initiation of cleavage cracks is linked to the process of coarse δ-ferrite and κ* phase. Finally, this paper summarized the controversial issues in Fe−Mn−Al−C medium Mn steels research and prospected the future development trend, to provide a reference for the follow-up research and actual production of medium Mn steels.
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图 1 Fe–11Mn–xAl–0.2C中锰钢力学性能随Al含量的变化
Figure 1. Mechanical properties of Fe–11Mn–xAl–0.2C steel with changes of Al content
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图 4 Fe–Mn–Al–C系中锰钢力学性能与工艺的关系。（a）中锰钢在不同工艺下的强塑积和延伸率分布；（b）Fe–8Mn–3Al–0.5C两种工艺样品的工程应力应变曲线[47]
UTS—ultimate tensile strength；YS—yield strength；TE—total elongation；YR—yield ratio；PSE—product of strength and elongation
Figure 4. Relations between mechanical properties and processes of Fe–Mn–Al–C medium Mn steels: (a) PSE and TE distribution of Fe–Mn–Al–C medium Mn steels in different processes; (b) engineering stress–strain curves of two different processes in Fe–8Mn–3Al–0.5C[47]
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图 6 几种典型的Fe–Mn–Al–C系中锰钢组织。（a）Fe–6Mn–2Al–0.4C在750 ℃临界退火20 min的SEM组织[5]；（b）Fe–8Mn–6Al–0.2C在1000 ℃固溶处理2 h的SEM组织[41]；（c）Fe–10Mn–10Al–0.7C 在850 ℃退火1 h的SEM组织[9]
Figure 6. Typical microstructures of Fe–Mn–Al–C medium Mn steels: (a) SEM microstructure of Fe–6Mn–2Al–0.4C annealed at 750 ℃ for 20 min[5]; (b) SEM microstructure of Fe–8Mn–6Al–0.2C after solution treatment at 1000 ℃ for 2 h[41]; (c) SEM microstructure of Fe–10Mn–10Al–0.7C annealed at 850 ℃ for 1 h[9]
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图 9 Mn的质量分数为10%时通过实验（数据点[77-78]）以及基于FactSage 6.4（实线[72]）和CALPHAD（虚线[79]）计算得到的Fe–Mn–Al–C合金900 ℃热力学相图
Figure 9. Isothermal phase sections of Fe–Mn–Al–C alloys at 900 ℃ established by experiments (indicidual points[77-78]), calculated from FactSage 6.4 (solid lines[72]) and from CALPHAD approach (dotted lines[79]) when Mn content is 10%
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图 10 用3D呈现的Fe–Mn–Al–C钢在室温下基于成分的SFE图
Figure 10. Composition-dependent SFE map of Fe–Mn–Al–C steels at room temperatures presented in 3D
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图 12 Fe–Mn–Al–C系中锰钢的断裂机制。（a）Fe–8Mn–6Al–0.2C拉伸变形后的SEM断口形貌[41]；（b）Fe–8Mn–8Al–0.8C拉伸变形中复合断裂示意图[39]
RD—rolling direction；TD—transverse direction；FG—fine-grained region
Figure 12. Fracture mechanism of Fe–Mn–Al–C medium Mn steels: (a) SEM fractograph after tensile deformation in Fe–8Mn–6Al–0.2C[41]; (b) schematic illustration showing the formation of mixed fracture during tensile deformation for Fe–8Mn–8Al–0.8C[39]
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图 13 临界退火后的Fe–6Mn–3Al–0.3C–1.5Si钢在拉伸变形时的破坏形成模型[94]。（a）在UFG区的孔洞萌生模型；（b）类解理裂纹的形成模型
RD—rolling direction；ND—normal direction
Figure 13. Model for damage formation during the tensile deformation of intercritically annealed Fe–6Mn–3Al–0.3C–1.5Si steel[94]: (a) model for void initiation in the UFG constituent; (b) model for cleavage-like crack creation
表 1 不同组织类型Fe–Mn–Al–C中锰钢的化学成分和力学性能[53]
Table 1 Chemical compositions and tensile properties of various Fe–Mn–Al–C medium Mn steels by their microstructure[53]
Microstructure Main chemical composition Mechanical properties References Yield strength/
MPaTensile strength/
MPaTotal elongation/
%α-ferrite (+ κ-carbide) Fe–3.5Mn–5.8Al–0.3C 532 722 23.2 [54–60] α-ferrite + austenite (+κ-carbide) Fe–9Mn–5Al–0.3C 502 734 77 [61–68] α-ferrite + δ-ferrite + austenite +
martensite（+κ-carbide）Fe–8.1Mn–5.3Al–0.23C 561 949 54 [20–21,39,
41,69–71]
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