新型Q-P-T钢的高强塑性及工程实施的探索
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摘要
在徐祖耀院士提出的淬火-分配-回火(Q-P-T)热处理思想的指导下,本文设计了成分为0.256C-1.2Si-1.48Mn-1.5Ni-0.05Nb (wt.%)的低碳Q-P-T钢及其热处理工艺。同时,采用光学显微镜(OM)、扫描电镜(SEM)、透射电镜(TEM)、X射线衍射(XRD)、热模拟实验和力学性能测试等方法,研究了Q-P-T工艺中回火参数的选择对钢件力学性能和显微组织的影响,并着重探讨了Q-P-T钢在室温拉伸过程中加工硬化行为的特点;观察了Q-P-T钢在不同拉伸温度下力学性能和显微组织的演变规律,并对残余奥氏体的稳定性进行了重点分析;最后,分析了Q-P-T工艺在工业生产中应用的可能性,并在此基础上,尝试设计了12 mm和20 mm的高强度热轧中厚板的热处理工艺。本文主要研究成果如下:
首先,设计了低碳Q-P-T钢,其化学成分为:0.256C-1.2Si-1.48Mn-1.5Ni-0.05Nb(wt.%),同时参考了Speer等人提出的CCE热力学模型,理论预测了Q-P-T工艺的初始淬火温度,并采用热模拟实验的方法设计了相应的热处理工艺:奥氏体化温度为930℃,初始淬火温度为290℃,回火温度为350~450℃,回火时间为15~3600 s。结果表明,350℃短时(30 s)回火的Q-P-T工艺处理得到的钢件具有较高的抗拉强度,其抗拉强度值接近1500 MPa,同时断后延伸率仍能保持在14%,强塑积为21000 MPa%;而经425℃短时(30 s)回火的Q-P-T工艺处理的钢件具有较好的塑性,其断后延伸率可达17%以上,同时其抗拉强度仍能达到1265 MPa,强塑积为22000 MPa%。两种Q-P-T钢的微观组织均为位错型板条马氏体和薄片状残余奥氏体,且细小的碳化物弥散分布在马氏体基体上,起到了一定的析出强化作用。其中,350℃短时回火Q-P-T钢的碳化物主要为HCP型ε过渡型碳化物,而425℃短时回火Q-P-T钢的碳化物则主要为FCC型(B1型)NbC微合金碳化物。然而,在经历425℃长时(3600 s)回火的Q-P-T工艺处理后,钢件中残余奥氏体的含量减少,生成了渗碳体(Fe3C)颗粒,钢件的力学性能也发生了下降。此外,分析了Q-P-T钢在室温拉伸过程中的加工硬化行为的特点。Q-P-T钢的加工硬化速率随应变的增加而下降,且在高应变时,加工硬化速率的下降趋势变缓,并出现较长的平台区。加工硬化指数则呈现三阶段变化,三个阶段分别为快速下降阶段,平台阶段和二次下降阶段。而残余奥氏体在拉伸过程中发生的马氏体相变及产生的TRIP效应则可能是Q-P-T钢在拉伸过程中加工硬化行为呈现上述变化的原因。
其次,重点研究了经Q-P-T工艺(初始淬火温度为290℃,回火工艺为425℃/30 s)处理后的试样在不同拉伸温度下的力学性能和显微组织的变化规律。结果表明,在-85~25℃拉伸时,试样展现了良好的低温稳定性,整个温度区间内,具有不亚于室温的力学性能;在25~300℃拉伸时,试样呈现了优异的强塑性,且在200℃时各项力学性能值达到峰值,抗拉强度为1300 MPa,屈服强度为940 MPa,断后延伸率和强塑积则分别为22%和28600 MPa%;当拉伸温度在300℃以上时,试样的力学性能开始发生恶化。对比室温显微组织可知,-85℃时,试样中各相均未发生显著变化,这也是Q-P-T钢在-85℃拉伸时仍具有良好强塑性的一个主要原因;200℃时,残余奥氏体含量略有减少,且在马氏体板条上析出了大量的ε过渡碳化物,残余奥氏体显著的TRIP效应和ε过渡碳化物的析出强化作用共同提高了Q-P-T钢的强度和塑性;400℃时,板条马氏体发生回火软化,板条变宽,部分残余奥氏体发生分解,含量下降,渗碳体在马氏体板条上和条间形成,三者共同导致了Q-P-T钢力学性能的恶化。此外,本文还着重分析了试样中残余奥氏体在不同拉伸温度下稳定性的变化特点,并依靠实验数据结合理论分析,得到了表征其稳定性的四个特征温度值,即,低温马氏体转变温度Ms<-85℃,残余奥氏体分解温度MT = 300℃,应力状态下残余奥氏体开始向马氏体转变的温度Msσ= 0℃,残余奥氏体在应力作用下不发生马氏体相变仅发生塑性变形的温度Md = 473℃。
最后,对Q-P-T工艺在工程中实施的可能性进行了探讨,从理论上说明了在连续冷却过程中也存在着碳分配效应,即连续冷却过程也可以稳定一定量的残余奥氏体,并结合“预冷+水淬+空冷自回火”的热处理方法为两种不同尺寸的热轧中厚板设计了相应的热处理工艺。其中,为模拟热轧中厚板的在线连续冷却过程,在实现20 mm热轧中厚板的热处理过程时采用了上海交通大学设计的穿水淬火冷却设备。显微组织表征结果显示,热轧中厚板经热处理后,其显微组织主要为马氏体、残余奥氏体和NbC,且随着钢件尺寸的增大,靠近心部的区域开始出现贝氏体。拉伸结果表明,两种中厚板的屈服强度均达到900 MPa以上,抗拉强度在1200 MPa以上,同时具有15%以上的延伸率,展现了良好的强塑性,达到设计的性能。可以说,常用的“预冷+水淬+空冷自回火”的热处理过程中在一定程度上也存在Q-P-T效应,这在设计高强热轧中厚板热处理工艺时显示了一定的潜力,而这也为Q-P-T工艺设计思想在工业生产中的推广提供了参考依据。
According to the Quenching-Partitioning-Tempering (Q-P-T) process proposed by T. Y. Hsu (Xu Zuyao), new types of low carbon high strength steels with adequate plasticity and toughness were obtained through different Q-P-T processes. Meanwhile, the effects of tempering parameters on the microstructures and mechanical properties of Q-P-T steels were investigated by optical microscopy (OM), scanning electron microscopy (SEM), transmission electron microscopy (TEM), X-ray diffraction (XRD), Gleeble thermal simulator and Zwick/Sans universal testing machines, and the work-hardening behaviors during plastic deformation were also analyzed. Additionally, the characteristics of microstructurures and the retained austenite stability of Q-P-T steels under different tensile temperatures were revealed. Lastly, a possibility on the application of Q-P-T processes in engineering was explored, and two proper Q-P-T processes for 12 and 20 mm thick hot-rolled plates were designed, respectively. The main research achievements are described as follows.
Firstly, a low carbon Q-P-T steel was designed, and its composition was measured as 0.256C-1.2Si-1.48Mn-1.5Ni-0.05Nb (wt.%). Based on the“Constrained Carbon Paraequilibrium”(CCE) theory proposed by Speer et al. and the related experimental data,proper Q-P-T process parameters were determined: initial quenching temperature was set to 290℃, and partitioning / tempering temperature was ranged from 350 to 450℃with the corresponding time ranged from 15 to 3600 s. The results indicated that this Q-P-T steel exhibited the highest ultimate tensile strength (UTS) (1500 MPa), sufficient ductility (14%) and product of strength (21000 MPa%) for tempering at 350℃for 30 s; and the best ductility (17%) and PSE (22000 MPa%) with superior UTS (1265 MPa) for tempering at 425℃for 30 s. The microstructures of the Q-P-T steel consisted of dislocation-type lath martensite and flake-like retained austenite with dispersively distributed carbides in martensite matrix, but the carbides changed from HCP-typeεtransition carbides to FCC-type (B1) NbC carbides with increasing tempering temperature. Especially for tempering at 425℃for 3600 s, the properties of the steel were deteriorated due to the formation of cementite (Fe3C) from the decomposition of retained austenite. In addition, the work-hardening behaviors of the Q-P-T steel during plastic deformation were also analyzed. The results showed that work-hardening rate decreased as tensile strain increased and its downward trend slowed down to a platform at higher strain, while work-hardening exponent presented a three-stage change including a first rapid decreasing stage, a plateau stage before necking and the last slow-decrease stage. The work-hardening behaviors mentioned above were attributed to the transformation induced plasticity (TRIP) effect of retained austenite.
Secondly, the microstructures and mechanical properties of the steel subjected to Q-P-T process (tempering at 425℃for 30 s) under different tensile temperatures were investigated in detail. When deformed at -85~25℃, samples exhibited good low-temperature properties almost the same as that deformed at room temperature. Samples deformed at 25~300℃showed excellent combinations of strength and ductility, and the mechanical properties reached the peak values at 200℃with the UTS of 1300 MPa, the yield strength (YS) of 940 MPa, the ductility of 22% and the PSE of 28600 MPa%. However, when tensile temperature increased to over 300℃, the mechanical properties tended to lower. By comparing with microstructure deformed at room temperature, it was found that the microstructure deformed at -85℃almost kept unchanged,which was the reason that Q-P-T steel exhibited good low-temperture properties. When the tensile temperature was set to 200℃, both the TRIP effect of retained austenite and the precipitation strengthening effect ofεtransition carbides contributed to the best combination of strength and ductility. However, when the tensile temperature rose to 400℃, the temper-softening of lath martensite, the decomposition of retained austenite and the formation of Fe3C occurred simultaneously, which led to the deterioration of mechanical properties. In addition, the stability of retained austenite in Q-P-T samples under different tensile temperatures was analyzed in detail, and its four characteristic temperatures were determined combining with experimental data, namely, Ms<-85℃, MT= 300℃, Msσ= 0℃and Md = 473℃.
Lastly, the possibility of Q-P-T processes applied in engineering was explored, and a new Q-P-T process with“pre-cooling + water quenching + air cooling”method for the continuous quenching process of hot-rolled plates was developed. According to this method, two proper Q-P-T processes for 12 and 20 mm thick hot-rolled plates were designed, respectively. The results showed that the microstructures of the as-treated plates consisted of martensite, retained austenite and NbC carbides, and some bainite formed near the core of the plates as the dimension increased from 12 mm to 20 mm. These two types of hot-rolled plates exhibited good mechanical properties with YS higher than 900 MPa, UTS higher than 1200 MPa and elongation more than 15%, which reached the design objective. The exploration of the Q-P-T process with“pre-cooling + water quenching + air cooling”method provided a reference for the applications of Q-P-T processes in engineering.
首先,设计了低碳Q-P-T钢,其化学成分为:0.256C-1.2Si-1.48Mn-1.5Ni-0.05Nb(wt.%),同时参考了Speer等人提出的CCE热力学模型,理论预测了Q-P-T工艺的初始淬火温度,并采用热模拟实验的方法设计了相应的热处理工艺:奥氏体化温度为930℃,初始淬火温度为290℃,回火温度为350~450℃,回火时间为15~3600 s。结果表明,350℃短时(30 s)回火的Q-P-T工艺处理得到的钢件具有较高的抗拉强度,其抗拉强度值接近1500 MPa,同时断后延伸率仍能保持在14%,强塑积为21000 MPa%;而经425℃短时(30 s)回火的Q-P-T工艺处理的钢件具有较好的塑性,其断后延伸率可达17%以上,同时其抗拉强度仍能达到1265 MPa,强塑积为22000 MPa%。两种Q-P-T钢的微观组织均为位错型板条马氏体和薄片状残余奥氏体,且细小的碳化物弥散分布在马氏体基体上,起到了一定的析出强化作用。其中,350℃短时回火Q-P-T钢的碳化物主要为HCP型ε过渡型碳化物,而425℃短时回火Q-P-T钢的碳化物则主要为FCC型(B1型)NbC微合金碳化物。然而,在经历425℃长时(3600 s)回火的Q-P-T工艺处理后,钢件中残余奥氏体的含量减少,生成了渗碳体(Fe3C)颗粒,钢件的力学性能也发生了下降。此外,分析了Q-P-T钢在室温拉伸过程中的加工硬化行为的特点。Q-P-T钢的加工硬化速率随应变的增加而下降,且在高应变时,加工硬化速率的下降趋势变缓,并出现较长的平台区。加工硬化指数则呈现三阶段变化,三个阶段分别为快速下降阶段,平台阶段和二次下降阶段。而残余奥氏体在拉伸过程中发生的马氏体相变及产生的TRIP效应则可能是Q-P-T钢在拉伸过程中加工硬化行为呈现上述变化的原因。
其次,重点研究了经Q-P-T工艺(初始淬火温度为290℃,回火工艺为425℃/30 s)处理后的试样在不同拉伸温度下的力学性能和显微组织的变化规律。结果表明,在-85~25℃拉伸时,试样展现了良好的低温稳定性,整个温度区间内,具有不亚于室温的力学性能;在25~300℃拉伸时,试样呈现了优异的强塑性,且在200℃时各项力学性能值达到峰值,抗拉强度为1300 MPa,屈服强度为940 MPa,断后延伸率和强塑积则分别为22%和28600 MPa%;当拉伸温度在300℃以上时,试样的力学性能开始发生恶化。对比室温显微组织可知,-85℃时,试样中各相均未发生显著变化,这也是Q-P-T钢在-85℃拉伸时仍具有良好强塑性的一个主要原因;200℃时,残余奥氏体含量略有减少,且在马氏体板条上析出了大量的ε过渡碳化物,残余奥氏体显著的TRIP效应和ε过渡碳化物的析出强化作用共同提高了Q-P-T钢的强度和塑性;400℃时,板条马氏体发生回火软化,板条变宽,部分残余奥氏体发生分解,含量下降,渗碳体在马氏体板条上和条间形成,三者共同导致了Q-P-T钢力学性能的恶化。此外,本文还着重分析了试样中残余奥氏体在不同拉伸温度下稳定性的变化特点,并依靠实验数据结合理论分析,得到了表征其稳定性的四个特征温度值,即,低温马氏体转变温度Ms<-85℃,残余奥氏体分解温度MT = 300℃,应力状态下残余奥氏体开始向马氏体转变的温度Msσ= 0℃,残余奥氏体在应力作用下不发生马氏体相变仅发生塑性变形的温度Md = 473℃。
最后,对Q-P-T工艺在工程中实施的可能性进行了探讨,从理论上说明了在连续冷却过程中也存在着碳分配效应,即连续冷却过程也可以稳定一定量的残余奥氏体,并结合“预冷+水淬+空冷自回火”的热处理方法为两种不同尺寸的热轧中厚板设计了相应的热处理工艺。其中,为模拟热轧中厚板的在线连续冷却过程,在实现20 mm热轧中厚板的热处理过程时采用了上海交通大学设计的穿水淬火冷却设备。显微组织表征结果显示,热轧中厚板经热处理后,其显微组织主要为马氏体、残余奥氏体和NbC,且随着钢件尺寸的增大,靠近心部的区域开始出现贝氏体。拉伸结果表明,两种中厚板的屈服强度均达到900 MPa以上,抗拉强度在1200 MPa以上,同时具有15%以上的延伸率,展现了良好的强塑性,达到设计的性能。可以说,常用的“预冷+水淬+空冷自回火”的热处理过程中在一定程度上也存在Q-P-T效应,这在设计高强热轧中厚板热处理工艺时显示了一定的潜力,而这也为Q-P-T工艺设计思想在工业生产中的推广提供了参考依据。
According to the Quenching-Partitioning-Tempering (Q-P-T) process proposed by T. Y. Hsu (Xu Zuyao), new types of low carbon high strength steels with adequate plasticity and toughness were obtained through different Q-P-T processes. Meanwhile, the effects of tempering parameters on the microstructures and mechanical properties of Q-P-T steels were investigated by optical microscopy (OM), scanning electron microscopy (SEM), transmission electron microscopy (TEM), X-ray diffraction (XRD), Gleeble thermal simulator and Zwick/Sans universal testing machines, and the work-hardening behaviors during plastic deformation were also analyzed. Additionally, the characteristics of microstructurures and the retained austenite stability of Q-P-T steels under different tensile temperatures were revealed. Lastly, a possibility on the application of Q-P-T processes in engineering was explored, and two proper Q-P-T processes for 12 and 20 mm thick hot-rolled plates were designed, respectively. The main research achievements are described as follows.
Firstly, a low carbon Q-P-T steel was designed, and its composition was measured as 0.256C-1.2Si-1.48Mn-1.5Ni-0.05Nb (wt.%). Based on the“Constrained Carbon Paraequilibrium”(CCE) theory proposed by Speer et al. and the related experimental data,proper Q-P-T process parameters were determined: initial quenching temperature was set to 290℃, and partitioning / tempering temperature was ranged from 350 to 450℃with the corresponding time ranged from 15 to 3600 s. The results indicated that this Q-P-T steel exhibited the highest ultimate tensile strength (UTS) (1500 MPa), sufficient ductility (14%) and product of strength (21000 MPa%) for tempering at 350℃for 30 s; and the best ductility (17%) and PSE (22000 MPa%) with superior UTS (1265 MPa) for tempering at 425℃for 30 s. The microstructures of the Q-P-T steel consisted of dislocation-type lath martensite and flake-like retained austenite with dispersively distributed carbides in martensite matrix, but the carbides changed from HCP-typeεtransition carbides to FCC-type (B1) NbC carbides with increasing tempering temperature. Especially for tempering at 425℃for 3600 s, the properties of the steel were deteriorated due to the formation of cementite (Fe3C) from the decomposition of retained austenite. In addition, the work-hardening behaviors of the Q-P-T steel during plastic deformation were also analyzed. The results showed that work-hardening rate decreased as tensile strain increased and its downward trend slowed down to a platform at higher strain, while work-hardening exponent presented a three-stage change including a first rapid decreasing stage, a plateau stage before necking and the last slow-decrease stage. The work-hardening behaviors mentioned above were attributed to the transformation induced plasticity (TRIP) effect of retained austenite.
Secondly, the microstructures and mechanical properties of the steel subjected to Q-P-T process (tempering at 425℃for 30 s) under different tensile temperatures were investigated in detail. When deformed at -85~25℃, samples exhibited good low-temperature properties almost the same as that deformed at room temperature. Samples deformed at 25~300℃showed excellent combinations of strength and ductility, and the mechanical properties reached the peak values at 200℃with the UTS of 1300 MPa, the yield strength (YS) of 940 MPa, the ductility of 22% and the PSE of 28600 MPa%. However, when tensile temperature increased to over 300℃, the mechanical properties tended to lower. By comparing with microstructure deformed at room temperature, it was found that the microstructure deformed at -85℃almost kept unchanged,which was the reason that Q-P-T steel exhibited good low-temperture properties. When the tensile temperature was set to 200℃, both the TRIP effect of retained austenite and the precipitation strengthening effect ofεtransition carbides contributed to the best combination of strength and ductility. However, when the tensile temperature rose to 400℃, the temper-softening of lath martensite, the decomposition of retained austenite and the formation of Fe3C occurred simultaneously, which led to the deterioration of mechanical properties. In addition, the stability of retained austenite in Q-P-T samples under different tensile temperatures was analyzed in detail, and its four characteristic temperatures were determined combining with experimental data, namely, Ms<-85℃, MT= 300℃, Msσ= 0℃and Md = 473℃.
Lastly, the possibility of Q-P-T processes applied in engineering was explored, and a new Q-P-T process with“pre-cooling + water quenching + air cooling”method for the continuous quenching process of hot-rolled plates was developed. According to this method, two proper Q-P-T processes for 12 and 20 mm thick hot-rolled plates were designed, respectively. The results showed that the microstructures of the as-treated plates consisted of martensite, retained austenite and NbC carbides, and some bainite formed near the core of the plates as the dimension increased from 12 mm to 20 mm. These two types of hot-rolled plates exhibited good mechanical properties with YS higher than 900 MPa, UTS higher than 1200 MPa and elongation more than 15%, which reached the design objective. The exploration of the Q-P-T process with“pre-cooling + water quenching + air cooling”method provided a reference for the applications of Q-P-T processes in engineering.
引文
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