N含量对22CrMoH齿轮钢伪渗碳条件下晶粒度的影响

采用热处理试验研究了不同N含量对22CrMoH齿轮钢在930和980℃伪渗碳条件下晶粒度的影响。结果表明,低N含量试验钢在930℃伪渗碳条件下保温10h后出现混晶现象,在980℃伪渗碳条件下保温大于等于1h即出现混晶现象;而高N含量22CrMoH齿轮钢在930和980℃伪渗碳条件下保温10h以内均未出现混晶现象。     

高温渗碳齿轮钢的研究进展

常用齿轮钢渗碳温度为930℃,提高渗碳温度至1000～1050℃能显著缩短渗碳时间,但易引起晶粒长人,因此发展了通过Nb、Ti、B微合金化,细化钢原奥氏体晶粒的高温渗碳齿轮钢。文中介绍了国内外高温渗碳齿轮钢的钢种成分、工艺特点、高温渗碳层组织控制和钢的疲劳性能的研究进展。     

20CrMnTi钢有无稀土渗碳热处理表面强化层的组织及性能研究

20CrMnTi钢作为一种常规渗碳钢,广泛应用于机械、汽车等行业。本文以20CrMnTi钢材料为研究对象,对比研究了普通热处理、渗碳热处理、稀土渗碳热处理不同表面热处理工艺条件下的表面强化层的组织及性能。结果如下:在化学热处理中加入稀土元素在化学热处理中起到催渗的作用,可以有效的增加渗层深度、表面硬度和耐腐蚀性。对比实验中不同热处理的表层硬度,稀土含量为5%的稀土渗碳热处理在加强表面硬度上是效果最显著的。     

温锻和等温正火对20CrMnTiH3齿轮钢渗碳淬火后奥氏体晶粒度的影响

通过理化和原材料奥氏体晶粒度检验分析了温锻（880~930℃）加工工艺对20CrMnTiH3齿轮钢奥氏体晶粒长大的影响,得到温锻加工齿轮工序在后续890~920℃渗碳过程中该钢奥氏体容易异常长大,830℃渗碳淬火后转变为粗大马氏体组织。温锻后回火、普通正火工艺对渗碳淬火后20CrMnTiH3齿轮钢奥氏体晶粒粗大无改善效果,而通过950℃1 h空冷至650℃8h空冷的等温正火工艺可以避免渗碳淬火后粗大马氏体。     

高温渗碳齿轮钢的晶粒粗化行为

  为了开发适合980 ℃高温渗碳的齿轮钢，利用伪渗碳方法，研究了铌质量分数为0、0.036%、0.060%和0.100%的18Cr2Ni2Mo渗碳齿轮钢在930和980 ℃的晶粒粗化行为。结果表明，由于析出NbC钉扎晶界，铌微合金化可以显著细化试验钢在930和980 ℃奥氏体化后的晶粒尺寸，且随着铌质量分数增加，铌微合金化明显抑制试验钢在980 ℃长时间奥氏体化晶粒粗化倾向。添加0.100%Nb的18Cr2Ni2Mo齿轮钢在980 ℃奥氏体化20 h后，平均晶粒尺寸仍然在26 μm左右，适合于980 ℃高温长时间渗碳。     

T10A钢制冷拔无缝钢管内模盐浴渗钒

本文介绍T10A 钢作为冷拔内模基体材料,经不同温度、不同时间盐浴扩散渗钒工艺试验,制订930℃×6h 为冷拔内模渗钒的处理工艺。用金相显微镜分析了渗钒层组织。以及渗钒后淬火回火组织。并讨论了研磨抛光表面光洁度对使用寿命的影响,与45钢渗碳镀铬内模冷拔1Cr18Ni9Ti 钢管对比,使用寿命提高4～6倍。     

SAE8620H的淬透性对热处理变形的影响

利用C型缺口试样研究了不同淬透性的SAE8620H齿轮钢的渗碳热处理变形,并对C型缺口试样心部微观组织和硬度进行了分析.结果表明,SAE8620H齿轮钢在距淬火端9 mm处的硬度低于32HRC时,C型缺口试样心部主要为贝氏体组织,渗碳热处理变形较小;随着淬透性的提高,试样心部马氏体组织逐渐增加,渗碳热处理变形显著增大.不同淬透性的SAE8620H齿轮钢的相变组织不同,因而渗碳热处理变形不同.     

P22耐热管的热处理工艺研究

实验采用直径为377 mm,壁厚为18.5 mm的12Cr2Mo1R钢,用FORMASTOR-F快速热膨胀相变仪测定Ac3及CCT曲线,设计出不同的热处理制度,根据不同热处理制度下钢的组织及力学性能得到最终的热处理工艺。结果表明,P22钢种的正火温度控制在930~960℃,回火温度在760℃的热处理制度下,能够满足产品力学性能要求。     

探讨调质钢检验奥氏体本质晶粒度的实际意义

目前,在我国执行标准中对30CrMnSiA、40CrNiMoA和38CrA等调质用钢要求检验奥氏体(以下简称A体)本质晶粒度。A体本质晶粒度在YB27—77标准定义是:“当钢加热超过临界点以上某一个规定温度(930℃)时所具有的A体晶粒。A体晶粒度表示钢的A体晶粒在规定温度下长大的倾向”[1]在这基本定义的要求下,不管什么钢种,其实际热处理条件如何都要在930℃温度下,衡量A体晶粒度大小并由此鉴定钢材质量的好坏,这是不科学的。回顾A体晶粒度的研究历史就不难看出“本质晶粒度”的引入首先从渗碳钢开始的。     

MC5钢冷轧工作辊热处理工艺研究

对MC5冷轧辊用钢进行了调质试验研究、模拟感应加热淬火的试验研究。研究了轧辊的预备热处理工艺对感应加热淬火组织的影响,感应加热温度和时间对组织和硬度的影响。结果表明,适宜的调质工艺为：930℃淬火,690－720℃回火;最佳感应加热淬火温度为930－950℃,奥氏体化6分钟淬火即可达到或接近最高硬度。     

低碳微合金钢中超细组织的热稳定性分析

研究了经过新开发的弛豫-析出控制相变RPC技术得到的钢板在650℃等温回火过程中组织与性能的演变,并与经过930℃保温1h后再淬火（RQ）工艺处理后的钢板进行了对比。回火前两种钢板均为贝氏体和少量马氏体的复合组织,经过RPC处理后的钢板回火0．5h后,金相尺度下的组织没有明显变化,但硬度下降较快,在1～7h的回火过程中组织中局部区域出现板条合并现象,此阶段硬度值变化不明显,7h之后某些区域组织的板条特征趋于消失,出现了少量的多边形铁素体,硬度开始明显下降,回火20h后,大约一半的组织转化成了多边形铁素体。而经过RQ处理后的钢板回火前硬度虽然较低,但回火过程中软化速度极快,板条组织很快消失,最终获得全部的多边形铁素体组织。结果表明超细组织的热稳定性取决于其加热历史。     

奥氏体化温度对高碳含硅钢等温转变的影响

 采用XRD物相分析、金相组织观察及TEM精细组织分析研究了奥氏体组织结构状态对Fe-0.88C-1.35Si-1.03Cr-0.43Mn 钢中温等温相变鼻温和孕育期的影响,以及不同温度奥氏体化后240 ℃等温20 min试样的组织结构特征。试验发现,随着奥氏体化温度的升高,中温等温开始转变的鼻温移向更低温度并且相变孕育期缩短;不同温度奥氏体化后同为240 ℃等温20 min处理,虽然均形成由贝氏体铁素体亚条平行排列构成的束状贝氏体组织,但贝氏体组织的精细结构状态不同,突出的差别在于对应低温奥氏体化贝氏体亚条端部边界具有凸起结构,而对应高温奥氏体化贝氏体亚条端部边界较为平齐且呈现楔形结构。不能简单地以马氏体切变机制认识试验钢中贝氏体组织的形成。     

Effect of quenching temperature on the microstructure of Si-containing steel during quenching and partitioning

This study aims to investigate the effect of the 1-step quenching and partitioning( QP) process on the microstructure and the resulting Vicker's hardness of 0. 3C-1. 5Si-1. 5M n steel by using in-situ dilatometry,optical microscopy( OM),scanning electron microscopy( SEM),X-ray diffractometry( XRD),and Vicker 's hardness measurement. Systematic analyses indicate that the microstructure of the specimens quenched and partitioned at150 ℃,200 ℃,250 ℃,and 300 ℃ mainly comprises lath martensite and retained austenite. The dilatometry curve of the specimen partitioned at 150 ℃ is presumably ascribed to the formation of isothermal martensite. In the early stages of partitioning at 200 ℃,the nearly unchanged dilatation curve is closely related to the synergistic effect of isothermal martensite formation and transitional epsilon carbide precipitation. In the later stages of partitioning at200 ℃,the slight increase in the dilatation curve is due to the continuous isothermal martensite formation. With further increase in partitioning temperature to 250 ℃,the dilatation increases gradually up to 3600 s,which is related to carbon partitioning and lower bainite formation. Partitioning at a higher temperature of 300 ℃ causes a rapid increase in the dilatation curve during the initial stages,which subsequently levels off upon prolonging the partitioning time. This is mainly attributed to the rapid diffusion of carbon from athermal martensite to retained austenite and continuous formation of lower bainite.     

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Effect of heat treatment process on corrosion performance of plastic die steel P20 and mechanism for corrosion were studied by electrochemical test, electrochemical impedance spectrum test, weight loss test, neutral salt spray test, SEM, EDS and XRD. It is found that the steels with bainite/martensite quenched at 860?? by air cooling or martensite quenched at 860?? by oil cooling have better corrosion resistance than the steel with ferritic/martensitic quenched at 785?? by oil cooling. After the samples with bainite/martensite or martensite are tempered at 450 and 620?? respectively, martensite and bainite decompose and a lot of carbides precipitate, leading to a poor corrosion resistance. After electrochemical test, the outer layer of corrosion product on the surface of the samples is loose FeOOH and the inner layer is relatively dense Fe3O4. The anode reaction is mainly dissolution of Fe and the cathode reaction is generation of hydrogen. Pitting mainly occurs around inclusions in NaCl solution of 0. 5mol/L.     

On Various Aspects of Decomposition of Austenite in a High-Silicon Steel During Quenching and Partitioning

Using a Gleeble thermomechanical simulator, a high-silicon steel (Fe-0.2C-1.5Si-2.0Mn-0.6Cr) was laboratory hot-rolled, re-austenitized, quenched into the M _s–M _f range, retaining 15 to 40 pct austenite at the quench stop temperature (T _Q), and annealed for 10 to 1000 seconds at or above T _Q in order to better understand the mechanisms operating during partitioning. Dilatometer measurements, transmission electron microscopy, and calculations showed that besides carbon partitioning, isothermal martensite and bainite form at the partitioning temperature. While isothermal martensite formation starts almost immediately after quenching with the rate of volume expansion dropping all the time, the beginning of bainite formation is marked by a sudden increase in the rate of expansion. The extent of its formation depends on the partitioning temperature following TTT diagram predictions. At the highest partitioning temperatures martensite tempering competes with partitioning. Small fractions of bainite and high-carbon martensite formed on cooling from the partitioning temperature. The average carbon content of the austenite retained at room temperature as determined from XRD measurements was close to the carbon content estimated from the M _s temperature of the martensite formed during the final cooling.     

等温淬火温度对超细贝氏体钢组织及耐磨性的影响

设计了一种0.7C的低合金超细贝氏体钢,并通过膨胀仪、二体磨损实验、光学显微镜、扫描电镜、X射线衍射、激光扫描共聚焦显微镜及能谱仪,研究了不同等温淬火温度对超细贝氏体钢的贝氏体相变动力学、微观组织以及干滑动摩擦耐磨性的影响,揭示超细贝氏体钢在二体磨损条件下的耐磨性能和磨损机理.研究结果表明,不同等温温度下的超细贝氏体钢都由片层状贝氏体铁素体和薄膜状以及块状的残留奥氏体组成;随着等温温度的升高,超细贝氏体的相变速率提高,相变孕育期及相变完成时间缩短,但贝氏体铁素体板条厚度增加,残留奥氏体含量增加,硬度值有所降低;超细贝氏体钢磨损面形貌以平直的犁沟为主,主要的磨损机理为显微切削;不同等温温度下所获得的超细贝氏体的耐磨性能都优于回火马氏体,且随着等温温度的降低,耐磨性能提高.其中在250℃等温所获得的超细贝氏体钢具有最优的耐磨性能,其相对耐磨性为回火马氏体的1.28倍.这主要与超细贝氏体钢中贝氏体铁素体板条的细化及磨损过程中残留奥氏体的形变诱导马氏体相变（TRIP）效应有关.      

Influence of Plastic Deformation on Thermal Stability of Low Carbon Bainitic Steel

Bainite is metastable due to its high dislocation density,and consequently bainitic steel structures have the problem of thermal stability.Plastic deformation of bainite can further increase dislocation density and change dislocation configuration at the same time.The influence of plastic deformation on thermal stability of low carbon bainitic steel during isothermal holding at 650 ℃ was investigated with hardness analysis,in-situ tracing metallographic analysis and transmission electron microscopy.Bainite in the low carbon steel evolves into polygonal ferrite via recovery and recrystallization during isothermal holding at 650 ℃.There is a considerably long period(about 20h)between end of recovery and commencement of recrystallization of undeformed bainite,in which the hardness of the sample maintains a constant value slightly lower than that before reheating.Slight plastic deformation of bainite induces rearrangement of pre-existing dislocations and forming of low-energy dislocation cells inside bainite laths,which has little influence on thermal stability of bainite,whereas heavy plastic deformation results in obvious dislocation multiplication and accelerates recrystallization of bainite.Recrystallization of heavily-deformed bainite occurs preferentially at prior austenite grains boundaries.The samples subjected to heavy torsion exhibit obviously higher thermal stability than the samples subjected to heavy compression despite their same initial hardness,which can be attributed to different influences of torsion and compression on dislocations and boundaries of bainite.     

AM对低碳贝氏体钢等温相变和显微组织的影响

摘要：设计了马氏体起始相变温度（Ms）以上和以下5个不同温度等温淬火实验,研究了Ms以上和以下温度等温淬火对低碳贝氏体钢组织和相变动力学的影响。结果表明,试样在Ms以下等温淬火时,保温前生成的先马氏体（AM）显著缩短了等温贝氏体相变孕育期,加速贝氏体形核,细化贝氏体组织。然而,Ms以下等温淬火时,总的等温贝氏体相变动力学与先马氏体的体积分数（fAM）有很大关系,当fAM较低时,AM的形成缩短了贝氏体相变孕育期,加速了贝氏体相变,当fAM过高时,又阻碍贝氏体相变,延长贝氏体总的相变时间。最后,采用Austin Rickett(AR)和Johnson Mehl Avrami Kolgomorov(JMAK)动力学模型对等温贝氏体相变动力学进行分析,结果表明,与AR模型相比,JMAK模型更适用于本研究的实验结果。     

硼对780 MPa低碳贝氏体钢组织和力学性能的影响

试验低碳贝氏体钢（/%:0.08C,0.11~0.13Si,1.10~1.20Mn,0.008~0.009P,0.002S,0.21~0.23Ni,0.020~0.021Ti,0.003~0.004Nb,0~0.0010B,0.000 7~0.0008O,0.0031~0.0033N）由50kg真空感应炉熔炼,轧成45mm钢板,并经930℃淬火,610℃回火。研究了0.0010%硼对780 MPa低碳贝氏体钢45mm板组织和力学性能的影响。结果表明,硼可显著提高试验钢的淬透性,不含硼试验钢淬火后得到粒状贝氏体,0.0010%硼试验钢淬火后得到板条贝氏体。硼明显改善试验低碳贝氏体钢的力学性能,含0.0010%硼试验钢淬、回火后的抗拉强度834MPa和屈服强度771MPa远高于不含硼试验钢的抗拉强度702MPa和屈服强度591MPa,实际生产中应加入适量硼可使低碳贝氏体钢得到板条贝氏体。     

热处理工艺对100mm特厚07MnCrMoVR水电钢板组织性能的影响

对07MnCrMoR水电钢板的淬透性曲线进行了测定,利用淬火机和热处理炉对100 mm厚试验钢板进行了淬火和回火试验,并对试验钢进行了组织观察和力学性能测定。结果表明,随着试验钢距水冷端的距离增大,淬火组织由马氏体转变为粒状贝氏体,距离端部50 mm处转变为铁素体和粒状贝氏体的混合组织。试验钢板利用淬火机淬火后得到板条贝氏体+粒状贝氏体+先共析铁素体,回火后转变为铁素体+粒状贝氏体,同时大量的碳化物在铁素体基体和晶界处析出。试验钢最合理的热处理工艺为930℃ 30min水冷淬火,660℃ 60min空冷回火。