深冷处理时间对M2高速钢红硬性的影响

使用洛氏硬度计、X射线衍射仪、扫描电子显微镜和透射电子显微镜等手段研究了深冷处理时间对M2高速钢的硬度和红硬性的影响及其机理。结果表明：深冷处理提高了M2钢的室温硬度和红硬性,深冷12 h使650℃红硬性的改善最显著。随着深冷时间的延长残余奥氏体含量不断降低,其形貌由长条形块状转变为薄膜状分布在马氏体板条间;马氏体轴比和碳含量逐渐降低,孪晶马氏体细化;初生碳化物偏聚减少,析出的二次碳化物数量逐渐增多。二次碳化物数量的增多不仅使析出强化作用增强,还能抑制高温下马氏体的分解。同时,残余奥氏体向马氏体的进一步转变以及孪晶马氏体的细化,对室温硬度的提高和红硬性的改善也有一定的作用。     

航空齿轮钢16Cr3NiWMoVNbE的真空低压渗碳

对航空齿轮钢16Cr3NiWMoVNbE进行真空低压渗碳热处理,研究了真空渗碳、淬火、冰冷处理以及回火工艺对材料的组织和性能的影响。结果表明：实验钢经渗碳淬火处理后,从表面到心部的组织可分为碳化物区、碳化物与针状马氏体混合区、针状马氏体区和心部板条马氏体区。在碳化物区的晶界有大量的块状Cr碳化物析出,在析出位置Ni元素较少。在针状马氏体和板条马氏体基体中细小的析出物为Nb、V、Mo微合金元素的碳化物。从渗碳钢表面到心部,随着碳浓度的降低硬度曲线呈现先升高后降低的趋势,渗层深度为0.95 mm。冰冷处理使残余奥氏体进一步转化为马氏体,使实验钢的硬度大幅度提高。     

新型模具钢012Al在深冷处理过程中的组织转变

本文利用x-射线衍射分析及复型和薄膜透射技术研究了012Al钢经淬火后在深冷处理过程中的组织转变。结果表明,淬火后的残余奥氏体在深冷处理过程中部分转变成马氏体;深冷处理使马氏体发生分解,析出超细碳化物;同时伴有形变晶孪产生。     

P92钢表层纳米组织的热稳定性

本文通过表面纳米化处理(SMAT)在P92钢表层中形成纳米组织结构,研究了回火温度对表层纳米组织演化行为和析出行为的影响.结果表明:淬火态和回火态P92钢组织经过SMAT处理后沿深度方向依次是纳米层、剧烈变形层、最终过渡到正常组织.随后分别研究了淬火和回火态SMAT试样经不同温度回火后微观组织的再结晶及长大行为.经SMAT处理的铁素体纳米晶粒在550℃时仍能保持较好的纳米结构,甚至高达650℃时表层晶粒仍为纳米晶,当温度超过760℃时表层组织发生显著的再结晶和晶粒长大现象.纳米晶界能抑制淬火态P92钢在较低温度回火时M23C6碳化物的析出.纳米组织提高了高温回火过程中合金元素在铁素体中的扩散速率,加速了M23C6碳化物的长大过程.不同温度回火过程中SMAT纳米层中析出行为的变化将在本文中详细描述.     

深冷处理工艺对M2高速钢显微组织与性能的影响

对M2高速钢进行不同时间或循环三次的深冷处理，然后测量深冷处理前后试样的硬度、冲击韧性以及高温摩擦磨损性能，结合X射线物相分析、扫描和透射电子显微分析技术研究深冷处理工艺对M2高速钢硬度、红硬性、冲击韧性、高温耐磨性和组织的影响及机理。结果表明：深冷处理后，残余奥氏体含量降低，一次共晶碳化物分解，二次碳化物弥散析出，并且孪晶马氏体细化。因此，深冷处理后M2高速钢的室温硬度、红硬性、冲击韧性和高温耐磨性均得到提高。延长深冷时间和循环深冷处理均利于提升M2高速钢的性能。循环三次深冷后M2高速钢的显微组织的改善和性能的提升最明显。较未深冷试样，循环三次深冷后试样残余奥氏体含量降低50%,大尺寸一次碳化物数量减少75.2%,二次碳化物析出增加约296%,室温硬度提高2.27%,红硬性提高2.7%,冲击韧性提高15.6%,高温相对耐磨性提高140%。与一次长时间深冷相比，循环深冷处理在提升性能和降低成本方面更有优势。     

低碳微合金直接淬火钢的组织与力学性能

为了提高低碳直接淬火钢的强韧性能,对一种低碳Nb-V微合金钢进行了轧后直接淬火(DQ)和再加热淬火(RQ)热处理实验,分析了低碳直接淬火钢的的强韧化机理.采用光学显微镜、透射电子显微镜、硬度计、拉伸试验机以及冲击试验机研究了轧后热处理工艺对低碳Nb-V微合金钢组织和力学性能的影响.结果表明,DQ工艺钢马氏体板条间距细小,含有较多的位错亚结构,因此具有较高的强度和韧性.DQ工艺钢马氏体中的大量位错,促进了碳化物弥散析出,产生了显著的二次硬化效果.由于基体中固溶的Nb、V等元素推迟淬火马氏体在回火过程中的各种转变,以及回火时析出的细小弥散碳化物抑制马氏体铁素体回复、再结晶过程,DQ工艺钢表现出较高的回火稳定性.     

深冷处理改善高速钢性能及其机理研究

深冷处理是一种有效的热处理工艺方法,通过深冷处理后,能够比较显著地改善材料的力学性能和较大幅度地提高工件的使用寿命。深冷处理工艺在金属材料领域的应用已经越来越广泛。研究表明,深冷处理不仅可以使残余奥氏体减少,而且还可以细化马氏体孪晶,促使纳米级碳化物的析出,并附着在马氏体孪晶带上。深冷处理不仅可以提高材料的硬度,也能够使材料的韧性略有增加。经过深冷处理,能够有效促使残留奥氏体向马氏体转变,并且析出超微细碳化物,可以获得比较好的综合力学性能,显著提高高速钢刀具的使用寿命。本文介绍了深冷处理工艺的特点和它的发展情况,阐述了深冷处理工艺对高速钢材料的影响,并展望了深冷处理工艺的发展前景。     

深冷处理对碳钢表面Mo-Cr合金层摩擦性能的影响

介绍了一种在Q235钢表面进行等离子合金化及热处理工艺,获得表面高性能强化层的技术方法.通过该技术方法的处理,使Q235钢表面含有Mo,Cr,C合金元素,成分达到或接近冶金高速钢.该工艺技术的基本原理是在真空容器中,利用辉光放电的溅射现象,首先在Q235钢表面渗入合金元素Mo,Cr,表面含量分别达到12%(质量分数,下同)和4%左右,随后进行超饱和渗碳,使表面含碳量达到2.0%以上,合金化层成分接近钼系高速钢.合金层中的碳化物细小、均匀、弥散,无粗大的共晶莱氏体组织.Q235钢表面合金化后分别采用淬火 低温回火,淬火 2h深冷处理 低温回火两种工艺.结果发现,经深冷处理的试样表面硬度达到1600HV,明显高于未经过深冷处理试样的表面硬度.摩擦磨损实验表明,经深冷处理试样的滑动摩擦系数较未经深冷处理试样的要小,经深冷处理试样的耐磨性是未经深冷处理的1.6倍.     

一种多元低合金高碳钢的热处理组织及硬度的研究

对一种低合金高碳钢(0.81C,0.65Cr,0.89W,0.54Mo,0.23V)热处理组织及硬度研究表明,该钢退火具有多类型碳化物(M3C,M7C3,M23C6,M6C和MC),在800～840℃区间退火,处于γ相低温区原碳化物部分溶解和新碳化物重新形核生长过程,使碳化物颗粒超细化,平均尺寸0.33～0.34 μm.淬火时,因M3C、M23C6溶解于奥氏体的速度较快,在840～860℃淬火时,硬度可达HRC63～65;未溶碳化物M6C和MC(VC)有利于马氏体细化,但因其数量较少,淬火最高温度不易超过880℃.该钢在低温和中温回火有较好的抗回火性能,并能有效地促进残余奥氏体转变.该钢热处理过程组织结构特征能较好地以相平衡热力学计算结果进行解释.     

低合金调质钢在回火过程中的力学性能EI北大核心CSCD

研究了回火温度对低合金调质钢力学性能和显微组织的影响。结果表明:淬火态为具有自回火析出物的板条马氏体,具有良好的强韧性配合;在250℃左右回火后片状碳化物析出量增加,提高了屈服强度;在400℃回火后在板条界析出碳化物薄壳,导致回火脆性现象;高温回火后板条形态仍普遍存在,局部区域的板条合并成铁素体块晶。在550℃以上回火析出大量纳米碳化物,渗碳体明显粗化.细晶强化和析出强化是实验钢的主要强化方式。在回火过程中组织演变及析出物性质直接影响拉伸曲线特征和n值。     

热作模具钢DM的高温稳定性和热疲劳性能

研究了热作模具钢DM的高温稳定性和热疲劳性能。结果表明,DM钢在620℃热稳保温过程中马氏体板条内的薄片状M₃C型碳化物逐渐向条块状M₇C₃型碳化物转变,在板条的边界生成M₇C₃、M₂₃C₆型碳化物。DM钢的短循环周次热疲劳性能受控于位错重排和湮灭,长循环周次热疲劳性能受控于碳化物的粗化程度。DM钢中M₃C、M₇C₃、M₆C型碳化物的生成自由能分别为27765.5 J/mol、3841.5 J/mol、-7138.1 J/mol,表明在热稳保温与热疲劳试验过程中碳化物的演变机理一致,发生了M3C→M7C3→M6C类型演变。     

High speed steel produced by spray forming

In this paper, ASP2030 (A30) high speed steel (HSS) was produced by spray forming and the microstructure was studied by optical microscopy (OM), scanning electron microscopy (SEM), transmission electron microscopy (TEM), electron probe microanalysis (EPMA) and X-ray diffraction (XRD). The spray formed A30 (SF A30) steel exhibited a very uniform and fine microstructure consisting of martensite, retained austenite and uniformly distributed network carbides. Microstructure refining can be explained in terms of the rapid solidification of spray forming. M₂C, MC and M₆C type carbides were found in the as-sprayed A30 HSS by XRD and TEM. A uniform distribution of carbides was obtained after forging and annealing. The microstructure properties of SF A30 steel indicate that spray forming can be considered as a cost-effective route for the production of A30 steels and other highly alloyed steels.     

Microstructural evolution and corresponding property changes after deep cryotreatment of tool steel

The microstructural evolution and structure–property correlation subjected to deep cryotreatment of tool steel were studied. The results show that the retained austenite continues to transform into martensite almost but not complete at low temperature. The topography of retained austenite exhibits as a nanoscale thin film with a thickness range of 20–60?nm between the martensite laths. The changes of internal friction peaks have been explained well by the coupling model, which indicates that deep cryotreatment is not only removing retained austenite but also promoting the interstitial carbon atoms segregated to nearby dislocations under the shrinking strain energy. In addition, more carbides precipitated from the matrix during tempering in cryotreated samples and were verified by analyses of transmission electron microscopy.     

Influence of deep cryogenic treatment on microstructure and evaluation by internal friction of a tool steel

The Influence of deep cryogenic treatment (DCT) on microstructure of a tool steel was studied by means of in situ obviation and carbon extraction replica technique. The results obtained have been shown that the retained austenite is present in a thin film between the laths of martensite and stably exists even during prolonged soaking time in liquid nitrogen. The in situ obviation and carbon extraction replica shows the carbides were not precipitated directly in the process of deep cryogenic treatment. The internal friction indicates the carbon atoms segregate to nearby dislocations and produced strong interactions, including interstitial carbon atoms themselves and between the interstitial carbon atoms with time-dependent strain field of dislocations. The cluster of carbon atoms nearby the dislocations either act as or grow into nuclei for the formation of carbide on subsequent during tempering.     

Enhancement of the mechanical properties of EN52CrMoV4 spring steel by deep cryogenic treatment

The effect of the deep cryogenic treatment on the micro-structure and mechanical properties (tensile strength, toughness, residual stress and fatigue strength) of the medium carbon spring steel, which is subjected to different heat treatment steps, is investigated. Deep cryogenic treatment causes spring steel to keep compressive residual stress more efficiently due to an increase in the density of the crystalline defects, retardation in the stress relief after the phase transformations and nano-cluster carbide formations. If deep cryogenic treatment is applied before the tempering then the homogeneously distributed fine carbides form after the tempering and the grains remain relatively fine. The microstructure with homogeneously distributed fine carbides and fine grains cause spring steels to have simultaneously enhanced tensile strength, ductility and fatigue strength. If deep cryogenic treatment is applied after the conventional heat treatment (quenching+tempering), however, the coarse carbides form in the micro-structure and the improvement in the mechanical properties of the spring steel is limited.     

TEM study on precipitation and transformation of secondary carbides in 16Cr–1Mo–1Cu white iron subjected to subcritical treatment

High chromium white irons solidify with a substantially austenitic matrix supersaturated with chromium and carbon. The subcritical heat treatment can destabilize the austenite by precipitating chromium-rich secondary carbides and other special carbides. In the as-cast condition the eutectic carbides are (Fe,Cr)₇C₃ and (Fe_4.3Cr_2.5Mo_0.1)C₃. The initial secondary carbide precipitated is (Fe,Cr)₂₃C₆ after heat-treating at 853 K for 10 h. There are MoC, Fe₂MoC and -carbide precipitating, and (Fe,Cr)₂₃C₆ transforms to M₃C after 16 h at 853 K. The -carbide and (Fe,Cr)₂₃C₆ accomplish transformation to M₃C and the matrix changes from martensitic to pearlitic after 22 h at 853 K. Thereby, in the subcritical heat treatment process, the initial secondary carbide precipitated is (Fe,Cr)₂₃C₆, followed by -carbide, MoC and Fe₂MoC. In addition, there are two in situ transformations from (Fe,Cr)₂₃C₆ and -carbide to M₃C carbides.     

Effects of deep cryogenic treatment on property of 3Cr13Mo1V1.5 high chromium cast iron

Effects of deep cryogenic treatment on the microstructure, hardening behavior and abrasion resistance of 3Cr13Mo1V1.5 high chromium cast iron subjected to sub-critical treatment were investigated in this paper. The results show that deep cryogenic treatment after sub-critical treatment, the hardness and abrasion resistance of high chromium cast iron can be boosted obviously due to abundant retained austenite transforming into martensite and secondary carbides precipitation. In the course of sub-critical treatment with cryogenic treatment, the amount of precipitated secondary carbides was more than that in air cooling, and the secondary hardening peak advanced at a lower temperature. When abrasion resistance reach the maximal, there was about 20% retained austenite in microstructures. Cryogenic treatment can further reduce the austenite content but can not make retained austenite transform to martensite completely.