高强塑积Q-P-T钢及其强塑性机制的研究
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摘要
先进高强度钢的发展趋势是研发更高强度的Fe-Mn-Si系廉价钢并保持足够的塑性,以期实现钢件轻量化,达到节约原材料、节能减排的低碳经济目的。基于此,我们课题组徐祖耀院士在Speer等提出的淬火&分配(Q&P)钢基础上,强调析出强化的重要性,进一步提出了淬火-分配-回火(Q-P-T)热处理新思想。本文根据新型Q-P-T工艺的设计思想,设计出低、中碳含铌钢相关的成分和优化的工艺,开发出高于目前先进高强度钢25000 MPa%的强塑积,达到或超过新一代先进高强钢强塑积的理论预测值(30000 MPa%),并揭示其高强度高塑性机制。此外,不同温度下(-85～450℃)的力学性能测试及显微组织表征为拓展Q-P-T钢的使用范围打下了实验基础。主要的研究内容和成果如下。
1.设计出四种不同C(0.2和0.4 wt.%)或Nb(0.03和0.08 wt.%)含量的Fe-Mn-Si基Q-P-T钢,参考约束条件下碳平衡(CCE)理论,选择在室温时得到最大奥氏体量的最佳淬火温度,对试样分别进行了传统的淬火&回火(Q&T)和新型的Q-P-T热处理。拉伸结果表明,经Q&T处理的试样,碳含量的增加使其力学性能遵循通常的高强度-低塑性的规律。然而经Q-P-T处理后的试样却发现,碳含量的增加同时提高钢的强度和塑性,这不同于通常的高强度-低塑性规律。其中,成分为Fe-0.42C-1.46Mn-1.58Si-0.03Nb的试样其强塑积为31627 MPa%(抗拉强度为1558 MPa,延伸率达到20.3%),超过下一代先进高强度钢所定义的理论强塑积值。此外,与Q&T处理相比,同成分的钢经Q-P-T处理后,在稍微降低抗拉强度的前提下显著提高其延伸率。
2.经X射线衍射(XRD)分析、扫描电镜(SEM)和透射电镜(TEM)观察等方法揭示了Q-P-T处理和Q&T处理后试样具有不同力学性能的内在原因。新型Q-P-T工艺和传统Q&T工艺的差别就在于淬火温度(Tq)的不同,前者的淬火温度通常远高于后者(室温),这使得相同成分的试样经Q-P-T处理后能获得更多的残余奥氏体,同时有效地减少了由淬火应力产生的微裂纹,从而显著提高了试样的塑性。在Q-P-T处理的试样中,碳含量增加同时提高其强度和塑性的机理是,高的碳含量提高了马氏体的强度,其包括板条马氏体内更高的位错密度,更小的马氏体领域(Packet)尺寸和更多析出的碳化物;同时提高其塑性的原因是获得更多的残余奥氏体。
3.通过对中碳Q-P-T拉伸试样施加不同的应变量后,测定了其残余奥氏体的体积分数变化,结果表明,随应变量的增加,残余奥氏体量逐渐减少。此外,低碳和中碳Q-P-T试样的真应力-真应变曲线对比发现,在缩颈前中碳Q-P-T试样具有较长的均匀形变能力;加工硬化指数-真应变曲线清楚地显示两者的TRIP效应的差异,即在均匀形变( n =εu)前,硬化指数(n)在大的应变范围内增加,呈现出宽的平台。因此,中碳Q-P-T试样在拉伸中表现出较明显的TRIP效应。
4.通过X射线衍射线形分析(XLPA)方法测定了中碳Q-P-T钢中马氏体和残余奥氏体的平均位错密度随应变量的变化。应变增加到3%时,马氏体的平均位错密度从6.65×1014 m–2 (未拉伸)减小到5.25×1014 m–2,而残余奥氏体的平均位错密度从4.21×1014 m–2 (未拉伸)迅速增加到8.77×1014 m–2,且超过了马氏体内位错密度。结果表明,在均匀形变阶段(应变约在12%内),马氏体的位错密度低于未形变前,直到均匀形变以后才逐渐增加,而残余奥氏体中位错密度在整个形变中快速地增加。基于以上结果,提出在形变过程中残余奥氏体吸收位错效应(DARA效应),即在形变的初始阶段,由于外加应力的作用,马氏体中的部分高密度位错可以移动到相邻的残余奥氏体中,这被TEM观察到的横跨马氏体/奥氏体界面的平行的位错列所间接证明。因此,残余奥氏体增塑机制为:残余奥氏体的DARA效应使马氏体在均匀形变阶段处于“未形变状态”,由此有效地提高了马氏体的形变能力;随应变的增大,当局域产生应力集中,由此通过应变诱发马氏体相变产生TRIP效应;随着应变的进一步增大而产生微裂纹,在马氏体条间的残留奥氏体可有效地阻碍裂纹扩展。
5.在低碳和中碳Q-P-T钢中,一直冷到-70℃时电阻测量仍未发现马氏体相变的迹象,表明残余奥氏体的Ms温度很低;反之升温到200℃时,也未发现残余奥氏体发生分解现象。表明在较宽的温度范围内残余奥氏体具有足够的热稳定性。经不同温度拉伸测定获得中碳Q-P-T钢的Msσ=-20℃,Md≈200℃。低的Msσ有利于在该温度之上时钢件在搬运或制造过程中避免应力诱发马氏体相变的发生,使残余奥氏体在以后的服役中产生TRIP效应。而Md≈200℃,表明钢件在该温度使用时残余奥氏体具有热力学稳定性和TRIP效应的最佳结合。
6.通过对低碳和中碳Q-P-T钢在-85～450℃范围内进行力学性能测定,发现低碳和中碳Q-P-T钢均存在一个具有最佳强度和塑性的温度范围:100～300℃,尤其是中碳Q-P-T钢在200℃时强塑积高达57738 MPa%。这主要是由于在此温度下中碳Q-P-T钢的残余奥氏体具有较高的热力学稳定性,同时马氏体基体中继续析出弥散分布的NbC和ε碳化物。此外,在所研究的温度范围内,中碳Q-P-T钢的强塑积均比低碳的高。
7. Si的加入能在室温抑制脆性渗碳体的形成,但不能抑制在较高温度(如350℃)下残留奥氏体分解形成的渗碳体和过渡型ε碳化物开始转变成的渗碳体。
The requirements of the resource and energy savings and the reduction of carbon emission are pushing the development of low-cost Fe-Mn-Si based advanced high strength steel (AHSS). In order to reach a higher product of strength and elongation (PSE) than 25000 MPa% of the advanced high strength steels (AHSS), even to 30000 MPa% of the next generation AHSS predicted by Matlock and Speer, both the composition and process of low and medium carbon steels have been designed in this work based on the novel heat treatment manner, quenching-partitioning-tempering (Q-P-T), proposed by T. Y. Hsu (Xu Zuyao) several years ago. Attentions were paid to understand the relationship between mechanical property and microstructure, in particular the enhancement effect of retained austenite on ductility of Q-P-T steels. The purpose of this dissertation attempts to investigate the mechanism of high PSE (product of strength and elongation) in designed Q-P-T steels with optimized processing parameters. The mechanical performance at different temperature from -85°C to 450°C was also studied to understand the potential application range of the proposed Q-P-T steel. The main achievements are expressed below.
1. Four kinds of Fe-Mn-Si based steels with the addition of different carbon (nominal 0.2 or 0.4wt.% respectively) and niobium (nominal 0.03 or 0.08wt.% respectively) were designed in the present research. Based on the constrained carbon equilibrium (CCE) theory proposed by Speer et al., the maximum fraction of retained austenite as a function of quenching temperature (Tq) was calculated, and the optimized parameters of Q-P-T process were determined. The traditional quenching and tempering (Q&T) process was also employed to these steels designed for comparing with Q-P-T process. The results indicate that medium-carbon Q&T steel has higher ultimate tensile strength and lower elongation than low-carbon Q&T steel, which shows that the effect of carbon content follows the general behavior of high strength-low ductility. However, medium-carbon Q-P-T steel has the ultimate tensile strength of 1558 MPa and elongation of 20.3% (uniform elongation of 12.2%), which reach the theoretical value predicted by Matlock and Speer. Obviously, a novel Q-P-T process makes the effect of carbon content be different from the general behavior of high strength-low ductility. Besides, the strength and elongation of medium-carbon Q-P-T steel also are much higher than 1222 MPa and 15.2% (uniform elongation of 6.13%) of low-carbon Q-P-T steel. These results indicate that a novel Q-P-T process produced a positive effect of carbon content on both strength and ductility.
2. The origin of different mechanical properties between Q-P-T steels and Q&T steels was revealed by microstructural characterization with XRD, SEM and TEM. The only difference between Q&T and Q-P-T treatment is the quenching temperature (Tq) selected, and Tq in Q-P-T process is much higher than that (room temperature) in Q&T process. Microstructural analysis indicates that the high Tq correspond to the high fraction of retained austenite and low stress caused by quenching. These are favorable for the transformation induced plasticity (TRIP) caused by retained austenite and the low formation probability of micro-crack caused by quenching. The increase of carbon content in Q-P-T specimens is responsible for the high strength due to higher density of dislocation in martensite, smaller packet size of martensite and more carbides distributed in martensite matrix. Meanwhile, the increase of carbon content is responsible for the high ductility due to stronger TRIP effect. These are why Q-P-T steels exhibit much better in both strength and elongation than Q&T steels.
3. The volume fractions of retained austenite as a function of strain in medium-carbon Q-P-T steels were determined by XRD. The results indicate that the retained austenite fraction decreases with increasing strain, which verifies the occurrence of TRIP effect. While, the low-carbon Q-P-T steel demonstrates a weak TRIP effect owing to less retained austenite in it. The work-hardening exponent-true strain curves of medium-carbon and low-carbon Q-P-T steels clearly demonstrate the difference of their TRIP effects.
4. The average dislocation densities in both martensite and retained austenite in medium-carbon Q-P-T steel were calculated by X-ray linear profile analysis (XLPA). The XLPA results indicate that the average dislocation density (Mρ) in martensite falls from 6.65×1014 m–2 (0% strain) to 5.25×1014 m–2 (3% strain), while the the average dislocation density (Aρ) in retained austenite rapidly raises from 4.21×1014 m–2 (0% strain) to 8.77×1014 m–2 (3% strain) which exceeds that in martensite. The phenomenon can be explained by the dislocation absorption by retained austenite (DARA) effect proposed in this work, namely, the plenty of dislocations in martensite move into the neighboring retained austenite, in other words, the dislocations are‘absorbed’by nearby retained austenite. Furthermore, the amount of dislocation transported to retained austenite is larger than the amount of dislocation multiplication in martensite, as a consequence, the comprehensive result leads to the decrease of Mρand the rapid increase of Aρ. Since DARA effect makes the martensite be an“undeformation state”, the deformation ability of hard phase martensite is intensified. With further increase of strain, when the amount of transported dislocation to retained austenite is smaller than the dislocation multiplication in martensite, the competitive result leads to the gradual increase of Mρ. While in the case of soft retained austenite phase, Aρstill sharply increases and shows high work–hardening rate. The DARA effect is indirectly verified by TEM observation in which the dislocations athwart from martensite to retained austenite at their interfaces can be clearly observed. Therefore, the mechanism of ductility enhancement by retained austenite can be briefly described as follows. In uniform deformation stage, DARA effect makes the martensite be an“undeformation state”, the deformation ability of hard phase martensite is intensified. With increasing strain, when the stress caused by high dislocation density in local area reaches certain critical value, the strain–induced martensitic transformation will occur, which effectively relaxes the stress concentration in this area and avoids the formation of microcracks, which is the well–known TRIP effect. In sequent larger strain condition, once microcracks form in some high stress concentration areas and propagate, the retained austenite can block the propagation of microcracks, which is the well–known blocking microcrack propagation (BMP) effect.
5. The retained austenite in low-carbon and medium-carbon Q-P-T steels exhibits excellent thermal stability since it still does not transform to martensite at -70℃, especially the characteristic parameter ( M sσ) of mechanical stability of retained austenite is about -20℃, exhibiting good mechanical stability. In addition, the product of strength and elongation at room temperature for medium-carbon Q-P-T steel can be kept at 300℃, as a result, medium-carbon Q-P-T steel studied in this work can be employed in the range from -20℃to 300℃. Low Msσis favorable for avoiding the occurrence of stress-induced martensitic transformation in carrying or manufacturing of workpieces, and thus strong TRIP effect will be produced by strain-induced martensitic transformation from retained austenite above Msσ. While Md≈200℃, it indicates that the retained austenite in workpieces at/below this temperature exhibits the optimum combination of thermal stability of retained austenite and TRIP effect.
6. After Q-P-T treatment, both low-carbon and medium-carbon specimens were deformed at different temperature from -85°C to 450°C. a temperature zone with best strength and elongation values were found for both compositions: 100℃～300℃. Within this zone, the PSE of medium-carbon specimen always higher than that of low-carbon specimen, especially at 200°C, the PSE of medium-carbon specimen reaches 57738MPa%! In addition to the further strengthening by carbide precipitation at this temperature, a better plasticity in medium-carbon specimen again verifies the beneficial effect of retained austenite at an elevated temperature.
7. The addition of Si can suppress the formation of brittle cementite at room temperature, but cannot suppress the formation of cementite by decomposition of retained austenite or by transformation of transition carbide in relative high temperature, such as at 350°C.
1.设计出四种不同C(0.2和0.4 wt.%)或Nb(0.03和0.08 wt.%)含量的Fe-Mn-Si基Q-P-T钢,参考约束条件下碳平衡(CCE)理论,选择在室温时得到最大奥氏体量的最佳淬火温度,对试样分别进行了传统的淬火&回火(Q&T)和新型的Q-P-T热处理。拉伸结果表明,经Q&T处理的试样,碳含量的增加使其力学性能遵循通常的高强度-低塑性的规律。然而经Q-P-T处理后的试样却发现,碳含量的增加同时提高钢的强度和塑性,这不同于通常的高强度-低塑性规律。其中,成分为Fe-0.42C-1.46Mn-1.58Si-0.03Nb的试样其强塑积为31627 MPa%(抗拉强度为1558 MPa,延伸率达到20.3%),超过下一代先进高强度钢所定义的理论强塑积值。此外,与Q&T处理相比,同成分的钢经Q-P-T处理后,在稍微降低抗拉强度的前提下显著提高其延伸率。
2.经X射线衍射(XRD)分析、扫描电镜(SEM)和透射电镜(TEM)观察等方法揭示了Q-P-T处理和Q&T处理后试样具有不同力学性能的内在原因。新型Q-P-T工艺和传统Q&T工艺的差别就在于淬火温度(Tq)的不同,前者的淬火温度通常远高于后者(室温),这使得相同成分的试样经Q-P-T处理后能获得更多的残余奥氏体,同时有效地减少了由淬火应力产生的微裂纹,从而显著提高了试样的塑性。在Q-P-T处理的试样中,碳含量增加同时提高其强度和塑性的机理是,高的碳含量提高了马氏体的强度,其包括板条马氏体内更高的位错密度,更小的马氏体领域(Packet)尺寸和更多析出的碳化物;同时提高其塑性的原因是获得更多的残余奥氏体。
3.通过对中碳Q-P-T拉伸试样施加不同的应变量后,测定了其残余奥氏体的体积分数变化,结果表明,随应变量的增加,残余奥氏体量逐渐减少。此外,低碳和中碳Q-P-T试样的真应力-真应变曲线对比发现,在缩颈前中碳Q-P-T试样具有较长的均匀形变能力;加工硬化指数-真应变曲线清楚地显示两者的TRIP效应的差异,即在均匀形变( n =εu)前,硬化指数(n)在大的应变范围内增加,呈现出宽的平台。因此,中碳Q-P-T试样在拉伸中表现出较明显的TRIP效应。
4.通过X射线衍射线形分析(XLPA)方法测定了中碳Q-P-T钢中马氏体和残余奥氏体的平均位错密度随应变量的变化。应变增加到3%时,马氏体的平均位错密度从6.65×1014 m–2 (未拉伸)减小到5.25×1014 m–2,而残余奥氏体的平均位错密度从4.21×1014 m–2 (未拉伸)迅速增加到8.77×1014 m–2,且超过了马氏体内位错密度。结果表明,在均匀形变阶段(应变约在12%内),马氏体的位错密度低于未形变前,直到均匀形变以后才逐渐增加,而残余奥氏体中位错密度在整个形变中快速地增加。基于以上结果,提出在形变过程中残余奥氏体吸收位错效应(DARA效应),即在形变的初始阶段,由于外加应力的作用,马氏体中的部分高密度位错可以移动到相邻的残余奥氏体中,这被TEM观察到的横跨马氏体/奥氏体界面的平行的位错列所间接证明。因此,残余奥氏体增塑机制为:残余奥氏体的DARA效应使马氏体在均匀形变阶段处于“未形变状态”,由此有效地提高了马氏体的形变能力;随应变的增大,当局域产生应力集中,由此通过应变诱发马氏体相变产生TRIP效应;随着应变的进一步增大而产生微裂纹,在马氏体条间的残留奥氏体可有效地阻碍裂纹扩展。
5.在低碳和中碳Q-P-T钢中,一直冷到-70℃时电阻测量仍未发现马氏体相变的迹象,表明残余奥氏体的Ms温度很低;反之升温到200℃时,也未发现残余奥氏体发生分解现象。表明在较宽的温度范围内残余奥氏体具有足够的热稳定性。经不同温度拉伸测定获得中碳Q-P-T钢的Msσ=-20℃,Md≈200℃。低的Msσ有利于在该温度之上时钢件在搬运或制造过程中避免应力诱发马氏体相变的发生,使残余奥氏体在以后的服役中产生TRIP效应。而Md≈200℃,表明钢件在该温度使用时残余奥氏体具有热力学稳定性和TRIP效应的最佳结合。
6.通过对低碳和中碳Q-P-T钢在-85～450℃范围内进行力学性能测定,发现低碳和中碳Q-P-T钢均存在一个具有最佳强度和塑性的温度范围:100～300℃,尤其是中碳Q-P-T钢在200℃时强塑积高达57738 MPa%。这主要是由于在此温度下中碳Q-P-T钢的残余奥氏体具有较高的热力学稳定性,同时马氏体基体中继续析出弥散分布的NbC和ε碳化物。此外,在所研究的温度范围内,中碳Q-P-T钢的强塑积均比低碳的高。
7. Si的加入能在室温抑制脆性渗碳体的形成,但不能抑制在较高温度(如350℃)下残留奥氏体分解形成的渗碳体和过渡型ε碳化物开始转变成的渗碳体。
The requirements of the resource and energy savings and the reduction of carbon emission are pushing the development of low-cost Fe-Mn-Si based advanced high strength steel (AHSS). In order to reach a higher product of strength and elongation (PSE) than 25000 MPa% of the advanced high strength steels (AHSS), even to 30000 MPa% of the next generation AHSS predicted by Matlock and Speer, both the composition and process of low and medium carbon steels have been designed in this work based on the novel heat treatment manner, quenching-partitioning-tempering (Q-P-T), proposed by T. Y. Hsu (Xu Zuyao) several years ago. Attentions were paid to understand the relationship between mechanical property and microstructure, in particular the enhancement effect of retained austenite on ductility of Q-P-T steels. The purpose of this dissertation attempts to investigate the mechanism of high PSE (product of strength and elongation) in designed Q-P-T steels with optimized processing parameters. The mechanical performance at different temperature from -85°C to 450°C was also studied to understand the potential application range of the proposed Q-P-T steel. The main achievements are expressed below.
1. Four kinds of Fe-Mn-Si based steels with the addition of different carbon (nominal 0.2 or 0.4wt.% respectively) and niobium (nominal 0.03 or 0.08wt.% respectively) were designed in the present research. Based on the constrained carbon equilibrium (CCE) theory proposed by Speer et al., the maximum fraction of retained austenite as a function of quenching temperature (Tq) was calculated, and the optimized parameters of Q-P-T process were determined. The traditional quenching and tempering (Q&T) process was also employed to these steels designed for comparing with Q-P-T process. The results indicate that medium-carbon Q&T steel has higher ultimate tensile strength and lower elongation than low-carbon Q&T steel, which shows that the effect of carbon content follows the general behavior of high strength-low ductility. However, medium-carbon Q-P-T steel has the ultimate tensile strength of 1558 MPa and elongation of 20.3% (uniform elongation of 12.2%), which reach the theoretical value predicted by Matlock and Speer. Obviously, a novel Q-P-T process makes the effect of carbon content be different from the general behavior of high strength-low ductility. Besides, the strength and elongation of medium-carbon Q-P-T steel also are much higher than 1222 MPa and 15.2% (uniform elongation of 6.13%) of low-carbon Q-P-T steel. These results indicate that a novel Q-P-T process produced a positive effect of carbon content on both strength and ductility.
2. The origin of different mechanical properties between Q-P-T steels and Q&T steels was revealed by microstructural characterization with XRD, SEM and TEM. The only difference between Q&T and Q-P-T treatment is the quenching temperature (Tq) selected, and Tq in Q-P-T process is much higher than that (room temperature) in Q&T process. Microstructural analysis indicates that the high Tq correspond to the high fraction of retained austenite and low stress caused by quenching. These are favorable for the transformation induced plasticity (TRIP) caused by retained austenite and the low formation probability of micro-crack caused by quenching. The increase of carbon content in Q-P-T specimens is responsible for the high strength due to higher density of dislocation in martensite, smaller packet size of martensite and more carbides distributed in martensite matrix. Meanwhile, the increase of carbon content is responsible for the high ductility due to stronger TRIP effect. These are why Q-P-T steels exhibit much better in both strength and elongation than Q&T steels.
3. The volume fractions of retained austenite as a function of strain in medium-carbon Q-P-T steels were determined by XRD. The results indicate that the retained austenite fraction decreases with increasing strain, which verifies the occurrence of TRIP effect. While, the low-carbon Q-P-T steel demonstrates a weak TRIP effect owing to less retained austenite in it. The work-hardening exponent-true strain curves of medium-carbon and low-carbon Q-P-T steels clearly demonstrate the difference of their TRIP effects.
4. The average dislocation densities in both martensite and retained austenite in medium-carbon Q-P-T steel were calculated by X-ray linear profile analysis (XLPA). The XLPA results indicate that the average dislocation density (Mρ) in martensite falls from 6.65×1014 m–2 (0% strain) to 5.25×1014 m–2 (3% strain), while the the average dislocation density (Aρ) in retained austenite rapidly raises from 4.21×1014 m–2 (0% strain) to 8.77×1014 m–2 (3% strain) which exceeds that in martensite. The phenomenon can be explained by the dislocation absorption by retained austenite (DARA) effect proposed in this work, namely, the plenty of dislocations in martensite move into the neighboring retained austenite, in other words, the dislocations are‘absorbed’by nearby retained austenite. Furthermore, the amount of dislocation transported to retained austenite is larger than the amount of dislocation multiplication in martensite, as a consequence, the comprehensive result leads to the decrease of Mρand the rapid increase of Aρ. Since DARA effect makes the martensite be an“undeformation state”, the deformation ability of hard phase martensite is intensified. With further increase of strain, when the amount of transported dislocation to retained austenite is smaller than the dislocation multiplication in martensite, the competitive result leads to the gradual increase of Mρ. While in the case of soft retained austenite phase, Aρstill sharply increases and shows high work–hardening rate. The DARA effect is indirectly verified by TEM observation in which the dislocations athwart from martensite to retained austenite at their interfaces can be clearly observed. Therefore, the mechanism of ductility enhancement by retained austenite can be briefly described as follows. In uniform deformation stage, DARA effect makes the martensite be an“undeformation state”, the deformation ability of hard phase martensite is intensified. With increasing strain, when the stress caused by high dislocation density in local area reaches certain critical value, the strain–induced martensitic transformation will occur, which effectively relaxes the stress concentration in this area and avoids the formation of microcracks, which is the well–known TRIP effect. In sequent larger strain condition, once microcracks form in some high stress concentration areas and propagate, the retained austenite can block the propagation of microcracks, which is the well–known blocking microcrack propagation (BMP) effect.
5. The retained austenite in low-carbon and medium-carbon Q-P-T steels exhibits excellent thermal stability since it still does not transform to martensite at -70℃, especially the characteristic parameter ( M sσ) of mechanical stability of retained austenite is about -20℃, exhibiting good mechanical stability. In addition, the product of strength and elongation at room temperature for medium-carbon Q-P-T steel can be kept at 300℃, as a result, medium-carbon Q-P-T steel studied in this work can be employed in the range from -20℃to 300℃. Low Msσis favorable for avoiding the occurrence of stress-induced martensitic transformation in carrying or manufacturing of workpieces, and thus strong TRIP effect will be produced by strain-induced martensitic transformation from retained austenite above Msσ. While Md≈200℃, it indicates that the retained austenite in workpieces at/below this temperature exhibits the optimum combination of thermal stability of retained austenite and TRIP effect.
6. After Q-P-T treatment, both low-carbon and medium-carbon specimens were deformed at different temperature from -85°C to 450°C. a temperature zone with best strength and elongation values were found for both compositions: 100℃～300℃. Within this zone, the PSE of medium-carbon specimen always higher than that of low-carbon specimen, especially at 200°C, the PSE of medium-carbon specimen reaches 57738MPa%! In addition to the further strengthening by carbide precipitation at this temperature, a better plasticity in medium-carbon specimen again verifies the beneficial effect of retained austenite at an elevated temperature.
7. The addition of Si can suppress the formation of brittle cementite at room temperature, but cannot suppress the formation of cementite by decomposition of retained austenite or by transformation of transition carbide in relative high temperature, such as at 350°C.
引文
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