<strong>Fe-C-Ni</strong>体系膨胀应变能对马氏体转变的影响

doi:10.11900/0412.1961.2020.00443

金属学报

2022, Vol. 58

Issue (2): 175-183 DOI: 10.11900/0412.1961.2020.00443

研究论文

本期目录 | 过刊浏览

Fe-C-Ni体系膨胀应变能对马氏体转变的影响

陈维¹^,², 陈洪灿¹^,², 王晨充³, 徐伟³, 罗群¹^,²(

), 李谦¹^,², 周国治¹^,²

^1.上海大学材料科学与工程学院省部共建高品质特殊钢冶金与制备国家重点实验室上海 200444
^2.上海大学材料科学与工程学院上海市钢铁冶金新技术应用开发重点实验室上海 200444
^3.东北大学轧制技术及连轧自动化国家重点实验室沈阳 110819

Effect of Dilatational Strain Energy of Fe-C-Ni System on Martensitic Transformation

CHEN Wei¹^,², CHEN Hongcan¹^,², WANG Chenchong³, XU Wei³, LUO Qun¹^,²(

), LI Qian¹^,², CHOU Kuochih¹^,²

^1.State Key Laboratory of Advanced Special Steel, School of Materials Science and Engineering, Shanghai University, Shanghai 200444, China
^2.Shanghai Key Laboratory of Advanced Ferrometallurgy, School of Materials Science and Engineering, Shanghai University, Shanghai 200444, China
^3.State Key Laboratory of Rolling and Automation, Northeastern University, Shenyang 110819, China

引用本文:

陈维, 陈洪灿, 王晨充, 徐伟, 罗群, 李谦, 周国治. Fe-C-Ni体系膨胀应变能对马氏体转变的影响[J]. 金属学报, 2022, 58(2): 175-183.
Wei CHEN, Hongcan CHEN, Chenchong WANG, Wei XU, Qun LUO, Qian LI, Kuochih CHOU. Effect of Dilatational Strain Energy of Fe-C-Ni System on Martensitic Transformation[J]. Acta Metall Sin, 2022, 58(2): 175-183.

全文: PDF(2219 KB) HTML

摘要:

为探究马氏体转变膨胀应变能对马氏体转变起始温度(M_s)的影响以及实现对M_s的准确预测，采用热膨胀相变仪测定了Fe-C-Ni合金的膨胀曲线，通过三切线法得到M_s与奥氏体转变起始温度。采用OM观察和XRD技术分析了成分对马氏体转变后组织和晶格参数的影响规律。通过考虑C成分与Ni成分交互作用，修正了马氏体转变膨胀应变能模型。以马氏体转变化学驱动力(同成分bcc相与fcc相的Gibbs自由能差)与非化学驱动力(奥氏体的剪切应变能、奥氏体的膨胀应变能、马氏体的缺陷储能和奥氏体与马氏体的界面能)之和为0作为判据，计算了Fe-C-Ni体系的M_s。结果表明，C含量与Ni含量的增加会促进转变后bcc相的晶格膨胀，Ni含量的增加会使形成的马氏体的板条变细小。在C含量(原子分数)小于1.0%，Ni含量(原子分数)小于20%的Fe-C-Ni合金中，计算得到膨胀应变能在非化学驱动力中的平均占比为41.3%。使用修正后的模型计算Fe-C-Ni体系的M_s，预测误差为4.1%。

关键词 ： Fe-C-Ni体系, 马氏体转变起始温度, 膨胀应变能, 热力学计算

Abstract：

Ultrahigh-strength steels have been widely used in critical engineering structures in military and civilian applications owing to the combination of ultrahigh strength and excellent toughness. The martensitic transformation start temperature (M_s) is an important parameter for designing alloys; it describes the thermodynamic stability and transformation behavior of austenite, affecting the strength and toughness of the alloy. To explore the influence of dilatational strain energy during martensitic transformation on M_s and calculate M_s in the Fe-C-Ni system, the dilatational curves of Fe-C-Ni alloys are measured using a dilatometer. Three tangents method is used to calculate M_s and austenitic transformation start temperature. The influence of composition on microstructure and lattice parameters after martensitic transformation was analyzed using OM and XRD. The dilatational strain energy model in the nonchemical driving force of martensitic transformation is modified considering the interaction between C and Ni components. The M_s of Fe-C-Ni system was calculated using a thermodynamic model in which the sum of martensitic transformation chemical driving force (the difference of Gibbs free energy between fcc and bcc phases) and nonchemical driving force (shearing strain energy of austenite, dilatational strain energy of austenite, dislocation stored energy of martensite, and interfacial energy of austenite and martensite) is zero. These results show that increasing C and Ni contents promote lattice expansion of the bcc phase after transformation whereas increasing Ni content reduces the martensite lath. The average proportion of dilatational strain energy of austenite in nonchemical driving force is approximately 41.3% in Fe-C-Ni alloys with atomic fractions of C < 1.0% and Ni < 20%. The prediction error of M_s in the Fe-C-Ni system is 4.1% using the modified model.

Key words： Fe-C-Ni system martensitic transformation start temperature dilatational strain energy thermodynamic calculation

收稿日期: 2020-11-04

ZTFLH:

TG111.3

基金资助:国家自然科学基金项目(U1808208);上海大学省部共建高品质特殊钢冶金与制备国家重点实验室自主课题项目(SKLASS2020-Z01);上海市科学技术委员会项目(19DZ2270200)

作者简介: 陈维，男，1994年生，硕士

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https://www.ams.org.cn/CN/10.11900/0412.1961.2020.00443 或 https://www.ams.org.cn/CN/Y2022/V58/I2/175

表1 Fe-C-Ni合金的成分 (atomic fraction / %)

图1 不同C含量的Fe-C-Ni合金的膨胀曲线(a) 0.48%C (b) 0.90%C

图2 不同成分Fe-C-Ni合金显微组织的OM像(a) Fe-18.33%Ni-0.49%C (b) Fe-9.14%Ni-0.47%C (c) Fe-4.32%Ni-0.48%C(d) Fe-15.62%Ni-0.86%C (e) Fe-7.94%Ni-0.88%C (f) Fe-4.09%Ni-0.97%C

图3 Fe-C-Ni合金的XRD谱和计算的Fe-C-Ni合金bcc相的晶格常数

图4 Fe-C-Ni体系马氏体相变线膨胀率(ΔL / L)模型拟合曲线

图5 Fe-Ni体系实验值0.5(Ms + As)[36~40]与T0温度预测值(本工作与文献[41,42])比较以及计算的Fe-C-Ni体系Ms (Ms—马氏体转变起始温度，As—奥氏体转变起始温度，T0—化学驱动力为0时的温度)

图6 不同Ni含量的Fe-C-Ni合金Ms计算值与本工作和文献[11,43~45]实验值及3种模型对Fe-C-Ni合金Ms的计算值(本工作与文献[11,22])和实验值对比(实验数据来源：Fe-C[11,50~53]、Fe-Ni[36,46,54~56]、Fe-C-Ni[11,43,44,54])

图7 Fe-C-Ni合金在Ms处的非化学驱动力与膨胀应变能

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