钢中贝氏体相变理论研究的新进展

总结了近年来内蒙古科技大学在贝氏体相变领域的主要研究成果.指出过渡性是贝氏体相变的主要特征;提出了贝氏体和贝氏体相变的新定义;认为以往的热力学计算不准.贝氏体铁索体的相变驱动力约为905 J/tool;提出了切变一扩散整合机制,贝氏体相变的晶核是单相BF,不是共析分解,贝氏体铁索体(BF)在贫碳区形核,是贫碳的Pa的无扩散相变,不是切变过程,而是以界面替换原子热激活跃迁方式形核长大;钢中贝氏体碳化物(Bc)在γ/a相界面上形核,向奥氏体和铁索体中长大,最终被铁索体包围,是以原子热激活跃迁方式进行的扩散型相变.     

块状转变与钢中贝氏体相变的亲缘关系——再论贝氏体相变的切变扩散整合机制

应用JEM-2010高分辨电镜和Quanta-400型环境扫描电镜,运用试验与综合分析的方法,研究了纯铁的块状转变和钢中的贝氏体相变,通过对相变的形核、长大,贝氏体亚单元和组织的形成的综合研究和分析,认为贝氏体相变与块状转变存在亲缘关系.依靠随机涨落,形成贫碳区,贝氏体铁素体在贫碳的奥氏体中形核.Fe原子和替换原子通过热激活跃迁、界面扩散或切变等方式,重复产生亚单元.在亚单元边界处,富碳奥氏体析出碳化物或成为残留奥氏体.贝氏体相变机制具有过渡性,即切变扩散整合机制.     

过冷奥氏体转变时原子位移规律

研究过冷奥氏体转变时原子的位移方式具有重要理论价值.原子位移方式不同是区别相变机制的依据之一.过冷奥氏体转变为珠光体、贝氏体、马氏体等组织,最基本的区别是原子位移方式的不同,从高温到低温,原子位移方式是逐渐演化的.研究表明,三个相变中原子位移方式分别是:(1)高温区的共析分解是扩散型相变,原子每次位移距离为一个原子间距.界面扩散是主要位移方式;(2)贝氏体相变是过渡性相变,贝氏体铁素体的形成是无扩散过程,而贝氏体碳化物的形成是扩散过程.铁原子和替换原子进行热激活跃迁位移.原子位移距离小于一个原子间距,各原子位移矢量不等,界面控制.(3)马氏体相变是无扩散的,所有原子进行集体协同位移,原子每次移动距离远远小于一个原子间距.切变机制不正确.在晶格改组过程中,为调整应变能一般需要形成位错、孪晶或层错等亚结构.     

贝氏体相变机制的探讨

贝氏体相变理论争论多年.研究贝氏体相变机制具有理论意义.运用理论的综合分析的方法,从贝氏体相变的过渡性入手,讨论了贝氏体铁素体的形核、热力学、动力学以及组织形貌、亚结构等与相变机制的联系,认为贝氏体相变具有明显的过渡特征,提出贝氏体相变机制是过渡性质的扩散切变整合机制.     

钢中贝氏体相变热力学

应用综合理论分析的方法研究了钢中贝氏体相变热力学.指出以往的KRC,LFG模型不适于贝氏体相变驱动力的计算.在进行相变热力学分析的基础上,依据γ→αB γ1→BF γ1转变机制设计了新的计算模型,并估算了Bs温度下相变阻力为105 J/mol.指出相变不仅与驱动力有关,而且取决于原子扩散能力.在贝氏体上部温度区,可以依靠界面扩散进行台阶长大;在460 ℃以下的某一段温度,可能以原子热激活跃迁无扩散机制进行贝氏体铁素体形核-长大过程;在Ms点稍上一段温度,可能以切变方式进行.     

马氏体形核-长大机制的研究

学术界普遍认为马氏体相变机制是切变机制,但与实际基本上不符.从理论分析和实验观察两方面综合论证了切变机制的缺陷,指出：（1）表面浮凸是相变体积膨胀所致,不具备切变特征,表明切变机制缺乏实验依据;（2）马氏体相变驱动力不足以克服相变阻力.切变消耗的切变能量太大,达208~320×10^3J/mol,远大于相变驱动力;（3）马氏体相变晶体学形核模型和切变长大模型均难以解释实验现象.半个世纪来不断改进仍然与实际基本不符,故切变机制是不成功的,并非成熟的理论,应于摒弃.探讨了新机制,指出马氏体相变是原子集体、协同的、无扩散的热激活跃迁位移,在此过程中马氏体中产生极高的位错密度,计算可达10^15×cm-2,与奥氏体保持半共格.新机制符合热力学条件,在晶体学、形态学上可解释实验现象.     

马氏体切变学说的评价

到目前为止,材料学界普遍认为马氏体相变是切变过程,有人则认为切变机制是成熟的理论,其实不然．综合分析了1930年以来提出的所有切变机制,指出各切变机制均与实际不符合的缺点,尚未形成普遍成熟的理论,而是切变学说．将新发现的珠光体浮凸,结合贝氏体、马氏体表面浮凸现象,一并分析了浮凸的形成机制,认为形成表面浮凸的主要原因是各相比体积不同,相变时试样表面不均匀体积膨胀所致．表面浮凸是过冷奥氏体转变产物的普遍现象,因而指出马氏体的切变机制缺乏实验依据．马氏体相变中,原子是极为复杂的集体有组织的位移,不是简单的机械式的切变过程．     

钢中贝氏体相变的论争及前景

简单地阐述了钢中贝氏体相变理论研究的2个学派学术论争的情况，并对某些观点应用自然辨证法的哲学理论进行了分析和纠正，指出，珠光体分解与贝氏体相变有着本质的区别，贝氏体组织是整合系统，不是混合物．应当把“过冷奥氏体→珠光体、贝氏体、马氏体”转变系列作为一个整合系统采研究．贝氏体相变是属于扩散型和切变型相变之间的中间过渡型相变的总体认识，是统一认识的基本条件．贝氏体相变具有扩散一切变整合机制．     

再评马氏体相变的切变学说

从表面浮凸现象、切变模型、切变能量、切变阻力、相变驱动力等多角度综合分析了马氏体的切变机制的缺陷,指出：表面浮凸是试样表面的过冷奥氏体转变的一种普遍现象,马氏体表面浮凸与珠光体、贝氏体的浮凸比较,没有特殊之处,马氏体相变切变机制缺乏实验依据.所有的马氏体切变模型均不能与实际完全符合,以位向关系来设计切变模型缺乏实验基础.钢中马氏体相变的驱动力约为（1.18-1.714）×10^3J.mol-1.按照各种切变模型进行切变需要极大的切变能量,在（208-320）×10^3J.mol-1之间,为相变驱动力所不及.按照切变机制完成马氏体相变,其阻力太大,约2.335×10^3J.mol-1,因此相变驱动力难以克服相变阻力完成切变过程.这种切变机制得不到符合实际晶格参数的马氏体晶体和亚结构.需要研究马氏体相变的新机制.     

材料相变过程中的形核理论

形核过程作为一级不连续相变中的重要阶段,对其研究具有重要的理论和应用价值.从经典理论的提出,到现今各种经典理论的修正以及非经典形核理论的建立,已有近一个世纪的时间.立足于对形核理论的理解,从热力学和动力学两个方面对相变中的形核理论进行了阐述,并对一些重要公式进行了重新推导和诠释;结合实际相变过程,对形核理论中仍存在的问题及可能的解决方法进行了探讨.     

TEM and HREM study on the fine structure and the interfacial structure of bainite

The fine structure of bainite,the morphology and distribution of carbide in steels and the morphology of bainite in Cu-Zn-Al alloys have been investigated with TEM.The interfacial structure ledges and interfacial crystal lattice images of Cu-Zn-Al alloys have also been investigated with HREM.The addition of alloying microelements can fine the structure of bainitic ferrite markedly.The bainitic ferrite is composed of subunits or subchunks.The carbides differ in morphologies and are distributed in between laths,inside the plates and on the boundaries of subunits.There are abundant fine structures in bainitic ferrite.In the primary bainite of Cu-Zn-Al alloy there are interfacial structure ledges,the height of which is about 3 -40 nm,equal to 15-200 atomic layers.The phase transformation mechanism of bainite is discussed.     

CuZn合金贝氏体预相变内耗

用低频倒扭摆内耗法研究了ＣｕＺｎ合金中贝氏体预相变。发现在贝氏体孕期内发生了溶质原子偏聚并形成溶质的贫化区与富化区，在内耗谱上出现偏聚过程内耗峰和弛豫内耗峰，用相关态理论解释弛豫内耗峰的形成机理。     

Effect of zirconium addition on the austenite grain coarsening behavior and mechanical properties of 900 MPa low carbon bainite steel

The ultra-free bainitic microstructure of a 900 MPa low carbon bainitic Cu-Ni-Mo-B steel was obtained by a newly developed relaxation precipitation control (RPC) phase transformation processing.In a pan-cake like prior-anstenite grain,the microstructure consisted of lath bainite,a little of abnormal granular bainite,and acicular ferrite.The effect of zirconium carbonitrides on the austenite grain coarsening behavior was studied by transmission electron microscopy (TEM).The results show that,the lath is narrower with increasing cooling rate.The ratio of all kinds of bainitic microstructure is proper with the intermediate cooling rate;and Zr-containing precipitates distribute uniformly,which restrains austenite grain growing in heat-affected welding zone.     

Dynamic observation of bainite transformation in a Fe-C-Mn-Si superbainite steel

The dynamic observations of bainitic transformation in a Fe-C-Mn-Si superbainite steel were conducted on a high temperature laser scanning confocal microscope. It is indicated that the mutual intersection of bainite sheaves often occurs during growth of bainite ferrite, resulting in an interlocked bainite microstructure. Moreover, bainite transformation is promoted by higher austenization temperature and the longer and finer bainite platelets are obtained. Further, The average growth rate of bainite after austenization at 1 100 ° is calculated as 5.8 µm·s^?1. In situ observation investigation makes it possible to identify bainite transformation in real time during isothermal holding.     

热穿-热轧法生产的新型贝氏体中空渗碳钢的组织和性能

用热穿-热轧法制备了新型贝氏体中空钢．研究了热处理对新型贝氏体钢和渗碳处理对中空钢组织和性能的影响．结果表明：新型贝氏体钢正火＋低温回火热处理后的组织为贝氏体铁素体和奥氏体,淬火＋低温回火后的组织由马氏体、贝氏体和奥氏体组成;正火或淬火＋低温回火后,新型贝氏体中空钢具有良好的强韧性．正火＋低温回火后,中空钢的组织为贝氏体铁素体和残余奥氏体组织．新型贝氏体中空钢渗碳后空冷,渗层的组织为高碳马氏体和残余奥氏体组织,非渗层为贝氏体铁素体和残余奥氏体组织,实体中空钢具有较好的强韧性和渗碳效果．     

珠光体到贝氏体的演化

综合以往的科学研究结果,论述了从珠光体分解到贝氏体相变是1个逐渐演化的过程.批驳了扩散学派所说的贝氏体是共析分解产物,所谓贝氏体是珠光体转变的延续的观点.指出了珠光体与贝氏体在扩散、形核、动力学、组织形貌、亚结构等方面的区别.     

Microstructure evolution during reheating of a Nb-bearing steel II. Dislocation-precipitate interaction

Cooled in water after the isothermal relaxation of deformed austenite for different times, a Nb-bearing microalloyed steel always exhibits the synthetic microstructure in which bainitic ferrite dominates. Strain-induced precipitates do not occur in an unrelaxed sample while they distribute outside dislocations in the sample relaxed for long time. Most of the strain induced precipitates distribute along dislocations in the sample relaxed for proper time. After bainitic transformation, the dislocations formed in the deformed austenite remain to be pinned by the precipitates so that the thermostability of the bainitic ferrite is improved. Coarsening of the precipitates accompanied by their distribution density change has caused the first hardness peak of bainite during reheating. The second hardness peak is attributed to the precipitates, which nucleate in bainite. Dislocations inside the laths getting rid of the pinning of precipitates and their polygonization play the precursor to the evolution of microstructures during reheating.     

Microstructure evolution during reheating of a Nb-bearing steelⅡ. Dislocation-precipitate interaction

Cooled in water after the isothermal relaxation of deformed austenite for different times, a Nb-bearing microalloyed steel always exhibits the synthetic microstructure in which bainitic ferrite dominates. Strain-induced precipitates do not occur in an unrelaxed sample while they distribute outside dislocations in the sample relaxed for long time. Most of the strain induced precipitates distribute along dislocations in the sample relaxed for proper time. After bainitic transformation, the dislocations formed in the deformed austenite remain to be pinned by the precipitates so that the thermostability of the bainitic ferrite is improved. Coarsening of the precipitates accompanied by their distribution density change has caused the first hardness peak of bainite during reheating. The second hardness peak is attributed to the precipitates, which nucleate in bainite. Dislocations inside the laths getting rid of the pinning of precipitates and their polygonization play the precursor to the evolution of microstructures during reheating.