共析渗碳体结构与变形行为的透射电镜研究

通过大量钢铁材料的透射电子显微镜分析,研究了渗碳体结构与变形行为之间的关系,探讨了渗碳体层片厚度对珠光体强韧性影响的机理。结果显示：在变形时,厚片渗碳体常以层片堆垛的方式生长,变形时易于沿层片间被切断;薄片渗碳体则难以切断,通常以弯曲的方式来适应变形。     

PD3钢轨钢接触疲劳变形组织的TEM观察

在透射电镜下观察接触疲劳失效后不同状态的ＰＤ３钢轨钢的变形组织。结果表明，接触疲劳变形组织的主要特点是：珠光体片层间距减小，珠光体团被剪切分割成亚团，先析铁素体内形成位错胞结构；铁素体／渗碳体界面上存在高的位错密度；珠光体中渗碳体片发生变形与断裂。同时对珠光体片层间距与变形组织的关系进行了分析讨论。     

渗碳体形态对珠光体钢丝拉拔形变的影响

利用金相显微镜、扫描电镜、透射电镜、拉伸试验机、硬度计对比研究了渗碳体分别为层片状与球状时对珠光体钢丝拉拔形变过程和性能的影响。层片状渗碳体在拉拔形变过程中表现出一定的变形能力,随应变量的增加,层片状珠光体逐渐演变为纤维状,且组织中未发现明显缺陷。球状渗碳体在形变过程中自身并不发生变形,但会向拉拔方向转动,并在渗碳体/铁素体的两相界面处出现微观缺陷,而这与球状渗碳体钉扎位错引起的应力集中有关。2种珠光体钢丝的强度和硬度均随着拉拔应变量的增加而不断提高,层片状珠光体的拉拔硬化率更高。随着拉拔的进行,钢中开始形成110织构。与球状珠光体相比,层片状珠光体组织的110织构强度更强,且随着应变量的增大,二者织构强度差越来越大。     

V和Ti在高碳钢中的应用

研究了V、Ti在预应力钢绞线及钢丝用高碳钢线材中的应用。高碳钢盘条中加入微量的V、Ti,在降低了珠光体相变温度的同时使珠光体相变与贝氏体相变温度区间发生分离;V的加入可以在细化珠光体片层间距的同时,抑制晶界连续渗碳体的形成。V、Ti在高碳钢中主要以复合碳氮化物的形式在晶界铁素体及珠光体片层间弥散析出,同时有部分V以合金碳化物的形式存在于渗碳体片层中。高温区析出的Ti(C,N)对奥氏体晶粒的长大具有显著的抑制作用,V主要在低温区以碳氮化物的形式起到析出强化的作用,另有部分V原子与Cr类似,与渗碳体结合形成合金碳化物,起到了强化渗碳体的作用。     

轴承钢GCr15低温轧制组织研究

利用Gleeble2000热模拟机研究了轴承钢GCr15在不同形变温度条件下的形变奥氏体组织状态,分析了950℃的高温轧制和750℃低温轧制的室温组织区别,结果表明,高温轧制时奥氏体发生动态再结晶,室温组织珠光体晶粒较大,珠光体组织内的渗碳体片层清晰,生长有规则;低温轧制时轴承钢GCr15为奥氏体＋渗碳体双相区形变,奥氏体不发生动态再结晶,同时渗碳体沿晶界发生动态析出,呈断续和球状,室温组织网状和珠光体晶粒尺寸降低,渗碳体片层生长不规则。     

室温等径角挤压后共析珠光体钢的组织特性

用扫描电镜(SEM)、透射电镜(TEM)和X-射线衍射(XRD)方法研究了0.78C-1.03Cr共析珠光体钢Φ8mm×45mm试样两道次室温等径角挤压后所产生的显微组织变化。结果表明,一道次等径角挤压变形后,共析珠光体组织,由渗碳体不规则弯曲片层、直接剪断片层和局部变薄层组成。随变形道次增加,发生局部变薄与不规则弯曲珠光体片层比例加大,并且还引起渗碳体的部分溶解。     

合金元素钒对高碳钢丝组织与性能的影响

 钒对高碳钢丝的微观组织、力学性能及热稳定性具有显著的影响。钒元素在高碳钢中主要存在于渗碳体中,可以起到强化渗碳体的作用。添加钒元素有利于珠光体片层间距的细化,还可以增加渗碳体的热稳定性,从而抑制钢丝拉拔过程中渗碳体的分解。但在拉拔应变量较大时,富含钒的渗碳体片碎化严重,会加重钢丝在镀锌过程中的球化现象,而导致钒合金化钢丝与未添加钒元素的钢丝相比,无论镀锌与否,其扭转性能均明显下降。     

汽车安全带卷簧用热轧钢带的开发生产

根据性能要求,冶炼过程采用洁净钢冶炼技术,热轧过程严格控制轧制工艺,成功开发生产了汽车安全带卷簧用热轧钢带,产品质量检测表明,钢的化学成分控制较好,钢质纯净,夹杂物尺寸小,热轧钢带的组织为珠光体,无网状渗碳体,边部无全脱碳层,珠光体片层细且均匀,片层间距300～450 nm。     

热轧形变量对共析钢珠光体组织球化的影响

利用Gleeble 1500热模拟机进行热压缩试验,研究了不同热轧形变量下奥氏体区形变对共析钢后续珠光体相变组织球化的影响。结果表明,高温奥氏体区形变增加了奥氏体的形变储存能,导致C曲线左移,并且形变可以明显减小珠光体团直径,随应变量增大,珠光体片层间距减小,渗碳体厚度变薄,片层取向多样化。最终的等温球化试验表明,增大奥氏体形变量有利于珠光体的球化效果。     

论提高珠光体钢轨钢性能的途径

本文通过对国内外金属材料研究成果的综合分析,介绍了珠光体钢轨钢的组织、成份与性能间关系着重阐述了决定珠光体钢轨钢性能的是其组织的几何参数,即珠光体团尺寸、珠光体片层间距和渗碳体片厚度。同时指出了控制珠光体钢组织几何参数的基本途径:合金化、热处理和控制轧制。     

轴承钢珠光体球化的研究现状及发展趋势

概述了轴承钢球化退火在轴承生产中的作用,分析了珠光体由片层状转变为颗粒状的变化规律,讨论了片层渗碳体的打断、短棒状向颗粒状转变以及颗粒状熟化长大的热力学机制。结果认为珠光体球化工艺的不足,一是存在碳化物分布不均匀、尺寸大小存在差异等问题;二是退火工艺固定化、格式化等问题,未能适应轴承钢的发展;三是球化退火后的组织检验粗糙化、不够细致。球化工艺的发展趋势,一是要在轧钢或锻压生产阶段通过引入塑性变形或增大冷却过冷度等方法来保证片层组织更加均匀、细化,无网状渗碳体;二是要开发新的球化工艺,例如在有可能的条件内引入电场、磁场以及高温高压应力场等方法来改善球化工艺;三是要将球化组织的定量化检验标准化。     

Chromium partitioning during the austenite-pearlite transformation

Partitioning of chromium between cementite and ferrite during the austenite to pearlite transformation in a eutectoid steel containing 1.29 pct chromium has been studied using analytical electron microscopy. No partitioning occurred at the austenite-pearlite interface below 703°C (the no-partition temperature), while above this temperature chromium partitioned preferentially to cementite at the transformation front. Chromium segregation to cementite occurred at all transformation temperatures after pearlite had formed. Measurements of pearlite growth rate and interlamellar spacing have been made for a range of transformation temperatures, and used to examine the rate controlling process for pearlite growth below the no-partition temperature. Growth rates calculated assuming volume diffusion of carbon to be rate controlling were in reasonable agreement with measured growth rates, although the discrepancies between the rates could be accounted for by the partial involvement of interfacial diffusion. Formerly affiliated.     

Deformation induced pearlite transformation and dynamic spheroidization in a eutectoid steel

The microstructure evolution of a eutectoid steel during the deformation induced pearlite transformation of undercooled austenite was investigated by uniaxial hot compression simulation experiment. The effects of different deformation degree, deformation rates and deformation temperature on the deformation induced pearlite transformation were explored. The results indicate that the induced pearlite transformation can occur rapidly during the deformation, for the stress accelerates phase transition. With the increase of the deformation degree, the dislocation density and phase transition driving force in the microstructure are improved, accelerating the occurrence of phase transition and the process of cementite spheroidization. For the diffusion- controlled phase transition, the deformation rates decrease to prolong the deformation time, so the carbon atoms can diffuse sufficiently to obtain spheroidized cementite. At lower deformation temperature from A1 to Ar1, significant refinement of the fragmentation of cementite occurs due to the increase of supercooling and spheroidized time. The ultrafine microstructure of cementite particles can be obtained through the high deformation degree, low deformation rates and low deformation temperature. It is also observed that the pro- eutectoid ferrite nucleates along the austenite boundary in the process of deformation.     

A transmission electron microscopy study of copper precipitation in the cementite phase of hypereutectoid alloy steels

The precipitation of copper has been detected and studied in three of the main decomposition products of austenite: allotriomorphic grain-boundary cementite, pearlitic cementite, and Widmanstätten cementite plates. The investigation has been carried out on two high-alloy hypereutectoid steels containing copper contents of 1.0 and 2.5 wt pct. The main advantage of these high-alloy steels is that the parent austenite phase remains stable upon cooling to room temperature, thus preserving the parent phase and the parent/product interfaces in the microstructure for subsequent examination. Transmission electron microscopy (TEM) revealed that the copper precipitation occurs in proeutectoid allotriomorphic grain-boundary cementite in association with the transformation interface. The copper particles were dispersed in the form of rows (or sheets) within the allotriomorphs of cementite. Evidence for copper precipitate particles nucleated at structural features imaged at the growth interface was also obtained. Copper precipitation was found to occur in both the ferrite and cementite lamellae of pearlite, and again, examination of partially decomposed structures revealed copper particles nucleated at the austenite/pearlite transformation interface. In addition, copper particles were also observed at the ferrite/cementite interface of pearlite. Copper precipitation observed in Widmanstätten cementite plates revealed a precipitate-free midrib region in the plates and a higher concentration of copper particles toward the broad faces of the plate. Copper particles were also found located at coarse linear interface defects at the broad faces of the plate.     

Mechanism of Austenite Evolution During Deformation of Ultra-High Carbon Steel

The mechanism of transformation of austenite to cementite and pearlite during the deformation of ultra-high carbon steel was discussed. The results indicate that the pearlite and cementite can be induced by deformation between Acm to Arcm The transformation during deformation is still considered as a diffusion-controlled process. With the increase of time and reduction, the pearlite fraction increased. At the beginning of the transformation, the pearlite was lamelliform. When the rate of reduction was increased to 70%, some of the induced lamellar pearlite was broken up under deformation.     

Influence of on-line tempering parameters on microstructure of medium-carbon steel

A new process involving ultra-fast cooling(UFC)and on-line tempering(OLT)was proposed to displace austempering process,which usually implements in a salt/lead bath and brings out serious pollution in the industrial application.The optimization of the new process,involving the evolution of the microstructure of medium-carbon steel during various cooling paths,was studied.The results show that the cooling path affected the final microstructure in terms of the fraction of pearlite,grain size and distribution of cementite in pearlite.Increasing the cooling rate or decreasing the OLT temperature contributes to restraining the transformation from austenite to ferrite,and simultaneously retains more austenite for the transformation of pearlite.It is also noted that bainite was observed in the microstructure at the cooling rate of 45°C/s and the OLT temperature of 500°C.Through either increasing the cooling rate or decreasing the OLT temperature,the distribution of cementite in pearlite is more dispersed and grain is refined.Taking the possibility of industrial applications into account,the optimal process of cooling at 45°C/s followed by OLT at 600°C after hot rolling was determined,which achieves a microstructure containing nearly full pearlite with an average grain size of approximately 7μm and a homogeneously dispersed distribution of cementite in pearlite.     

Si在高碳钢盘条开发中的应用

研究了Si对高碳钢盘条珠光体相变及钢丝热稳定性的影响。研究表明,Si含量的增加可以明显地提高珠光体相变温度,且在高碳钢中增加相同含量的Si,不同相变温度下盘条硬度的增加值基本保持不变;三维原子探针分析结果表明,在高碳钢中添加一定量的Si可以减小盘条铁素体片层中C原子的偏聚程度,有利于提高C原子分布的均匀性;同时Si可以明显地提高渗碳体片层的球化温度,有利于钢丝热稳定性的提高。     

共析钢中铌对珠光体相变行为的影响

 通过金相、扫描电镜,相变临界点和过冷奥氏体等温转变的分析,研究了Nb对共析钢（质量分数：C 075%,C 0.78%）珠光体相变微观组织和等温转变动力学的影响。结果表明：微量Nb（质量分数为0.04%、0064%）的加入使钢中先共析铁素体的量较未含铌钢有所增加,这很可能是Nb的加入使得共析碳含量明显升高的结果,同时使珠光体相变产物的形貌发生明显变化,珠光体中渗碳体的展弦比显著降低。此外Nb提高了先共析铁素体和珠光体的开始转变温度,即Nb的加入在一定程度上降低了过冷奥氏体的热力学稳定性;相变动力学表明加入Nb 0.04%可使珠光体相变的鼻子点温度升高约50℃,且最快开始相变时间比不含铌钢推迟一个数量级以上,即Nb的加入推迟了鼻子点和较低温度下的珠光体相变,提高了钢的淬透性。     

Chromium partitioning during isothermal transformation of a eutectoid steel

Partitioning of chromium between ferrite and cementite during the isothermal decomposition of austenite to pearlitic or pearlitic/bainitic decomposition products has been studied in a 1.4 wt pct Cr eutectoid steel using analytical electron microscopy on two-stage extraction replicas. Chromium was observed to segregate preferentially to cementite at the pearlite reaction front for temperatures in the range 730 to 550 °C. Although the extent of partitioning decreased with decreasing reaction temperature, a no-partition temperature could not be identified for the steel. It is clear that previous studies on thin foils have underestimated the temperature range over which partitioning of chromium can occur. At high reaction temperatures measured values of pearlite growth rates were found to be in excellent agreement with those calculated, using the assumption that phase boundary diffusion of chromium was rate controlling. At lower reaction temperatures models based on volume diffusion of carbon and on phase boundary diffusion of chromium both gave reasonable predictions of measured growth rates. However, it seems likely that solute drag effects influence pearlite growth at temperatures in the austenite bay region which the chromium addition produces in the T.T.T. diagram. Measurements made on upper bainite which co-existed with pearlite following transformation at 500 and 550 °C showed that preferential partitioning of chromium to cementite did not occur during this reaction. Formerly Graduate Student, University of Manchester