关于高碳冷轧钢板中渗碳体的石墨化及C,P含量对它的影响

在一定的退火条件下，含Ｍｎ和Ｐ的钢格中的碳，经常以石墨的形式析出，由于渗碳体的减少和铁素体直径的增大，延伸性变得与Ｃ含量无关。为在较短的退火周期内，得到较好的延伸性石墨化钢板中渗碳体的石墨化及 本研究做了如下实验：采用０．１５％Ｓｉ－０．１５％Ｍｎ－０．００４％Ｓ冷轧钢板，它的Ｃ呈范围在０．０５－０．６５％之间，Ｐ含量范围在０．００１－０．０５％之间；退火温度在５５０－７００℃之间；退火时间在０．     

初始组织形态对中碳钢温变形组织演变的影响

中碳钢温变形过程的组织演变包含铁素体动态回复、再结晶和渗碳体的析出球化等过程.采用Gleeble1500热模拟试验机研究了初始组织形态对含碳0.48%(质量分数)的中碳钢在温变形中上述复杂过程的影响.结果表明:初始组织为珠光体+先共析铁素体的试样在温加工变形中渗碳体层片发生了扭折、溶断到逐渐球化的过程,在铁素体回复再结晶的同时伴随着细小弥散的渗碳体颗粒从过饱和铁素体中析出,得到微米级铁素体晶粒和颗粒状渗碳体弥散分布的复相组织,但等轴状铁素体晶粒与弥散的渗碳体颗粒沿变形方向呈带状不均匀分布.温加工变形促进初始组织为马氏体的中碳钢中渗碳体析出和铁素体回复与再结晶.由于初始条件下碳的分布在微观尺度下相对均匀,变形后获得细小等轴铁素体与均匀分布颗粒状渗碳体的组织.     

超高碳钢的回火组织及力学性能

用CM200型透射电子显微镜研究了超高碳钢双相区淬火 中、高温回火后的组织,用Instron型拉伸试验机测定了力学性能.结果表明:650℃的回火组织为等轴状的铁素体与球状的渗碳体,屈服强度σ0.2=1127MPa,抗拉强度σb=1 266 MPa,均匀伸长率δu=8.26%,总伸长率δt=9.71%,维氏硬度HV为397;450℃回火组织的铁素体保持淬火的形态,回火碳化物为ε碳化物在基体上以断续的片状析出,σ0.2=1 911 MPa,σb=2 028MPa,δu=δt=1.88%,HV为595;400℃回火组织中的铁素体保持淬火的形态,回火碳化物在位错处几乎呈网状析出,拉伸无塑性,HV为703.     

脉冲电流对球墨铸铁退火组织与性能的影响

在球墨铸铁的高温石墨化过程中采用脉冲电流为辅助手段,研究了脉冲电流对退火处理球墨铸铁力学性能以及渗碳体的石墨化、铁素体转变的影响.经脉冲电流处理后,球墨铸铁的硬度、抗拉强度降低,延伸率增加.SEM分析表明,脉冲电流加速了球墨铸铁的高温石墨化过程,促进了铁素体的转变.脉冲电流处理后石墨形核率的增加是加速渗碳体分解和铁素体转变的主要原因.     

0.2C-1.25Si-2.0Mn Q&P钢渗碳体的析出动力学分析

为研究Q&P(淬火-分配)钢临界区均热工艺对配分过程中渗碳体析出的影响,通过Avrami动力学方程对Q&P钢渗碳体析出的PTT(沉淀量-温度-时间)曲线进行了计算。通过热膨胀仪对Q&P钢进行了单相区退火、临界区退火,退火后淬火,并通过透射电镜检测室温下马氏体的衍射斑,计算马氏体的碳含量,以此推测高温下奥氏体中的碳含量。通过连续退火模拟机模拟了不同临界区退火的Q&P工艺。在扫描电镜下检测了析出渗碳体的尺寸,结合热处理工艺和渗碳体的熟化率计算了析出开始时间。由此得出了渗碳体析出体积分数5%的PTT曲线绝对位置。846℃均热的条件下鼻子点温度为300℃。811℃均热条件下,鼻子点温度上升至325℃,764℃均热条件下,鼻子点温度上升至400℃。在746～846℃均热,配分时间≤450 s的情况下,可以避免渗碳体的析出。     

石墨化碳素钢的冷压缩变形行为

利用Gleeble-3800热模拟试验机,在应变速率为1s~(-1)下,对以铁素体+石墨为组织特征的碳的质量分数为0.43%的石墨化碳素钢进行冷压缩变形试验。绘制了该钢的应力-应变曲线,并利用光学显微镜、场发射扫描电镜、显微硬度仪对不同压下量压缩试样中大变形区内石墨粒子的变形形态及其内部结构,以及铁素体的变形形态及其显微硬度进行了金相分析。研究结果显示,该钢在本试验条件下的应力-应变曲线中存在峰值应力,其峰值应力为645MPa,对应的即峰值应变为0.43;随着压下量的增加,压缩试样大变形区内石墨粒子、铁素体逐渐被压扁并呈纤维化,其中,变形石墨粒子的变形依靠石墨片层间的滑移变形、亚结构间的剪切变形以及压实石墨随铁素体基体流动的延伸变形来实现;铁素体的显微硬度随着压下量的增加而增大,呈逐渐硬化趋势,但峰值应力后的硬化程度减缓。结合铁素体的硬化程度以及变形石墨的内部结构,可以认为,峰值应力后,压缩试样大变形区的变形是以石墨变形为主,铁素体变形为辅(主要为协调石墨变形)的变形过程,这也是该钢应力-应变曲线中应力降低的原因之一。     

石墨化炉用原料及产品质量分析

为了评价某连续式石墨化炉产品质量,对原料生石油焦、煅后石油焦、石墨化焦进行了性能参数测定。结果表明:所测生石油焦和煅后石油焦的挥发分析出规律基本一致,温度在400～700℃范围内,挥发分析出速率较大,900℃之后,挥发分基本析出完全;石墨化焦的挥发分质量分数、灰分质量分数、碳质量分数和真密度分别为0.09%、0.1%、99.63%和2.19 g/cm~3,满足高纯石墨化焦的质量要求,说明该连续式石墨化炉的生产技术值得推广。最后简单阐述了原料性能参数对对石墨化炉操作工艺的影响。     

硅和铬对中碳钢贝氏体显微组织的影响

为了获得具有良好强度一韧性平衡弹簧钢的重要信息,检测了Si和Cr含量对中碳钢贝氏体显微组织的影响。将4种实际的中碳钢JIS-S55C、SUP9、SUP7和SUP12在1000℃奥氏体化后,在温度介于300oC和500℃之间进行等温转变,借助扫描电子显微镜以及透射电子显微镜观察显微组织。在没有Si和Cr的$55C钢贝氏体转变早期,形成碳化物,而在SUP7和SUPl2钢中,碳化物的析出受Si含量的增加而受到抑制。在贝氏体转变中期,由于残余奥氏体中的碳浓度增加,导致残余奥氏体的分数随Si和Cr的增加而增加。事实上,添加硅可促进游离碳化物贝氏体铁素体,并且通过碳的富集,导致残余奥氏体的数量较大。     

25Co15Ni11Cr2MoE钢回火过程中析出相的演变规律

采用透射电子显微镜(TEM)和X射线衍射仪(XRD)等试验方法对一种高Co-Ni二次硬化钢25Co15Ni11Cr2MoE淬火后经300~660℃温度范围回火后析出的合金碳化物和韧化相逆转变奥氏体的析出演变规律进行系统研究。结果表明:25Co15Ni11Cr2MoE经300~660℃温度范围回火后,随回火温度升高,钢中析出的合金碳化物依次为:弥散的ε-碳化物→片状的合金渗碳体→弥散的M2C碳化物→粗化的M23C6碳化物。经495℃回火后,钢中板条马氏体基体上析出大量细小弥散的M2C碳化物,回火早期析出的粗大片状渗碳体全部回溶,并在马氏体板条间析出薄膜状韧化相逆转变奥氏体。回火温度提高至530℃后,逆转变奥氏体含量继续增加,但其形貌逐渐由薄膜状转变为条、块状,回火温度提高到600℃时,钢中的逆转变奥氏体含量达到极大值。     

形变对板条马氏体回火组织的影响

对Q235级低碳钢板条马氏体在550℃多道次单向压缩变形后退火和室温大塑性变形轧制后在此温度退火的显微组织演变规律进行了对比研究,结合未变形板条马氏体在此温度的回火组织演变,讨论了变形对马氏体分解过程、铁素体再结晶晶粒尺寸和析出碳化物形貌的影响.实验结果表明,变形显著影响马氏体分解过程,促进渗碳体的析出和铁素体回复及再结晶.热变形组织铁素体再结晶晶粒尺寸在0.5μm左右;渗碳体形貌从细棒状向球状转变,随变形量增大渗碳体尺寸增大,继续保温60min导致铁素体晶粒长大到1μm左右,晶粒内部的渗碳体消失,原先在铁素体晶界析出的渗碳体球化、粗化.冷轧试样在550℃退火保温时间在30min内得到0.3~0.4μm超细晶粒和尺度小于150nm的弥散渗碳体颗粒组织;随退火保温时间延长到60min,铁素体再结晶晶粒长大到1.9μm,渗碳体颗粒尺寸约160nm.     

A study on inhomogeneous distribution of temper graphite particles in strip-cast Fe-C-Si alloys

This study examined the relationship between solidification structure and graphitization characteristics of white cast iron strips produced by strip casting. Experimental results showed that there was an unusual distribution of temper graphite particles along the through-thickness direction of the graphitized strips in comparison with gravity-cast chill plate. In particular, the graphite-free zones appeared in the vicinity of the strip surface after the completion of graphitization, especially in the strip with low carbon and silicon content. There were abnormally straight interfaces between matrix and eutectic cementite with a strong preferred [001]_c growth direction caused by the effect of directional solidification found in the near-surface regions of the strips. The interfaces did not form a site for the graphite to nucleate and gave rise to the graphite-free zones close to the strip surface. An increase in carbon and silicon content could significantly increase the number of temper graphite particles and shorten the time for the completion of graphitization, but an inhomogeneous distribution feature of graphite particles was still observed in strips with a higher carbon equivalent value (CE). Furthermore, variations in carbon and silicon content resulted in transitions in carbide morphology and composition, which had a tremendous effect on the graphitization characteristics of the cast iron strips.     

Transformation of Carbides in Prolonged Rail Operation

The evolution of the carbide phase in the surface layers of bulk-quenched rails (after the passage of 500 and 1000 million t of traffic) and differentially quenched rails (after the passage of 691.8 million t) to a depth of 10 mm at the central axis of the rail cross section and at the nearby rounded section is studied by transmission electron-diffraction microscopy. The grains of plate pearlite, ferrite–carbide mixture, and structure-free ferrite are analyzed. The carbide phase in the surface layers of the steel changes in two mutually complementary processes during rail operation: (1) cleavage of cementite particles with subsequent entrainment in ferrite grains or plates (in the pearlite structure); (2) cleavage and dissolution of cementite particles, with transfer of carbon atoms to dislocations (in Cottrell atmospheres and in dislocational cores), which transport them to the ferrite grains (or plates), where cementite nanoparticles are formed again. In the previous location of the plates, fragmented dislocational substructure appears. The boundaries of the fragments are found at the positions previously occupied by cementite α-phase boundaries. The solution of cementite is mainly due to the energy of carbon atoms at dislocation cores and subboundaries in comparison with the cementite lattice. The binding energy of the carbon atom and the dislocations is 0.6 eV and the binding energy of the carbon atom and the subboundary is 0.8 eV, as against 0.4 eV for the carbon atom in cementite. Elastoplastic stress fields are formed; their stress concentrators are intra- and interphase boundaries of ferrite and pearlite grains, cementite plates and ferrite of the pearlite colonies, and globular cementite and ferrite particles. Those are also the basic sources of curvature and torsion in the crystal lattice of the rail steel. On approaching the contact surface, the number of stress concentrators increases, and the internal long-range stress fields are of greater amplitude.     

Redistribution of Carbon Atoms in Differentially Quenched Rail on Prolonged Operation

The change in structure, phase composition, and defect substructure in the head of differentially quenched rail after the passage of gross traffic amounting to 691.8 million t is investigated over the central axis, at different distances from the top surface, by means of transmission electron microscopy. The results confirm that prolonged rail operation is accompanied by two simultaneous processes that modify the structure and phase composition of the plate-pearlite colonies: cutting of the cementite plates; and solution of the cementite plates. The first process involves cutting of the carbide particles and removal of their fragments, accompanied simply by change in their linear dimensions and morphology. The second process involves the extraction of carbon atoms from the crystal lattice of cementite by dislocations. That permits phase transformation of the metal in the rail, which is associated with marked relaxation of the mean binding energy of the carbon atoms at dislocations (0.6 eV) and at iron atoms in the cementite lattice (0.4 eV). The stages in the transformation of the cementite plates are as follows: the plates are wrapped in slipping dislocations, with subsequent splitting into slightly disoriented fragments; the slipping dislocations from the ferrite lattice penetrate into the cementite lattice; and the cementite dissolves with the formation of nanoparticles. The cementite nanoparticles are present in the ferrite matrix as a result of their transfer in the course of dislocational slip. On the basis of equations from materials physics and X-ray structural data, the content of carbon atoms at structural elements of the rail steel is assessed. It is found that prolonged rail operation is accompanied by significant redistribution of the carbon atoms in the surface layer. In the initial state, most of the carbon atoms are concentrated in cementite particles. After prolonged rail operation, the carbon atoms and cementite particles are located at defects in the steel’s crystalline structure (dislocations, grain and subgrain boundaries). In the surface layer of the steel, carbon atoms are also observed in the crystal lattice based on α iron.     

Microstructure and Properties of Graphitized Free-Cutting Steel

This article describes the metallographic studies and the tensile tests of quenched and high-temperature tempered samples of graphitized free-cutting steel and the experience of machining graphitized samples. The experimental results have shown that the microstructure of the graphitized steel is comprised mainly of ferrite and graphite, and graphite particles are distributed both along grain boundaries and inside them. The morphology of graphite is presented by a spherical shape (average diameter of ~10 μm). The ratio of the yield stress to the ultimate strength is 0.59, and the machinability coefficient is k_T = 5.4241. The microstructure of steel samples after quenching and high-temperature tempering is comprised mainly of secondary sorbite. In this case, the ratio of the yield stress to the ultimate strength is 0.82.     

Rapid graphitization of a pulsed laser remelted ductile cast iron during multipass overlap melting

As-cast ductile cast iron with an as-machined shiny metal surface was remelted with a high-power (1 kW) pulsed Nd:YAG laser using both single- and multipass overlap melt tracks. Changes in the microstructure of the underlying laser melted track caused by the transient overlap heating during multipass overlap remelting process were studied. The rapidly solidified metastable ledeburite structure of the underlying laser melted track was found to be rapidly graphitized during overlap remelting. The graphitized zone consists of a fully graphitized zone containing extremely fine graphite nodules and a partially graphitized zone containing extremely fine graphite nodules and undissolved cementite. The overlap ratios of the melt tracks were shown to have no noticeable influence on either the graphitized microstructure and the size of the graphitization zones. This newly observed rapid graphitization phenomenon is preliminarily discussed in terms of the microstructural characteristics of the rapidly solidified ductile iron and the unique heating behavior of pulsed laser beam to material.     

Cold deformation behavior of graphitized carbon steel

The cold compression test of a strain rate 1s-1 for graphitized carbon steel containing C of 0. 43 mass% with ferrite and graphite was carried out using Gleeble- 3500 thermal simulation machine, the characteristics of the stress- strain relationship was analyzed, and metallographic analysis in the large deformation zone of the compressed samples with different reduction was investigated by optical microscope, field emission scanning electron microscopy and micro hardness tester. The results show that there exists peak stress on the stress- strain curve, namely, 645MPa, the corresponding peak strain is 0. 43; in process of the compressive deformation, morphologies of ferrite and graphite in the large deformation zone on the longitudinal section of the compressed samples gradually become fibrous with increasing the reduction; thereinto, the deformation of graphite particles is realized by means of sliding deformation between basic planes of graphite, shear deformation between substructures of graphite particles, as well as elongation of compacted section near the base of the ferrite of the deformed graphite particles; microhardness of ferrite increases with increasing the reduction, it indicate that ferrite is in a state of hardening, but, increase amplitude of microhardness in the process of compressive deformation after peak stress is decreased. Therefore, based on increase amplitude of microhardness of ferrite and microstructure of the deformed graphite particles, it can be concluded that in process of the compressive deformation after peak stress, deformation of graphite particles in the large deformation zone plays a major role, a deformation of ferrite plays a secondary role (it is mainly to coordinate the deformation of graphite particles), this is one of the main reason that stress decreases in the compressive deformation after peak stress.     

Long-term operation surface changes in differentially quenched 100-m rails

By optical microscopy and transmission electron diffraction microscopy, the evolution of the structural and phase states in the surface layers over a depth of 10 mm in the head of differentially quenched rail (category DT350) is studied, as the rail is subjected to passed tonnage of 691.8 million t at the experimental loop of AO VNIIZhT. In the initial state, the following structural components are present in the rail head: plate-pearlite grains (relative content 0.7); mixed ferrite–carbide grains (0.25); and grains of structure-free ferrite. After experiencing a passed tonnage of 691.8 million t, this state only remains beyond a depth of 10 mm. At that depth, a large quantity of bend extinction contours is observed. That indicates elastoplastic distortion of the material’s crystal lattice. The stress concentrators in the steel are intraphase and interphase boundaries of the ferrite and pearlite grains, cementite and ferrite plates in pearlite colonies, and globular cementite and ferrite particles. Structural transformations are observed at the macro level: microcracks appear, running at acute angles from the surface to a depth of 140 μm; and a decarburized layer is formed. At the micro level, elastoplastic stress fields are formed, and the cementite plates in the pearlite colonies break down. The stress concentrators in that case are intraphase and interphase boundaries of the ferrite and pearlite grains, cementite and ferrite plates in pearlite colonies, and globular cementite and ferrite particles. In structure-free ferrite grains, cementite nanoparticles are formed. The results are compared with the evolution of the structural and phase states at the surface of a recess in bulk-quenched rail as the rail is subjected to gross loads of 500 million t: the transformation of the structural and phase states in the surface layers is more pronounced. Plate pearlite is characterized by solution of the cementite plates. That leads to the formation of chains of globular carbide particles at the sites of the cementite plates. This may be associated with transfer of the carbon atoms from the cementite lattice to dislocations.     

亚共析石墨化易切削钢的开发

 石墨易切削钢是顺应易切削钢无铅、低硫这一发展趋势而提出的。具有亚共析组织的钢种其石墨化过程一直很难,因此该钢种开发的关键是促进其石墨化过程。基于增加石墨核心来加速石墨化过程进行了钢种的成分设计与研制。结果表明,正是开发钢中具有与石墨结构（简单六方）相同的BN成为了石墨的形核位置,从而有效促进了开发钢的石墨化过程。开发钢的组织由铁素体和石墨组成,其中,石墨的缺口效应和润滑效果赋予了开发钢较高的切削性能和冷成形性能。