超纯铁素体不锈钢热变形过程中的析出行为

利用热力模拟实验机及试验轧机研究了添加Ti,V的超纯中铬铁素体不锈钢热变形过程中的析出行为变化特点,并采用热动力学计算及透射电子显微镜观察来表征析出相特征.结果表明:热变形过程中形成的析出相主要为TiC,这与热动力学分析一致.这些析出相的特征与变形温度密切相关,随着变形温度的降低,析出相TiC尺寸更加细小且分布更加弥散.这主要是由于变形温度降低时扩散速率相对较低,不利于析出相长大,而晶体缺陷增加,形变诱导析出的有效形核位置增加.这一热变形过程中的析出行为变化规律在中试试验条件下得到了验证.     

高强贝氏体钢测定R_(P0.2)准确性分析

对高强贝氏体钢在拉伸检测过程中影响测定RP0.2准确性的检测方法、检测设备和检测材料三个因素进行了分析。通过严格控制检测材料加工的平行度和加工面的平整度,及时更换磨损过度的钳口套和钳口并保证充分润滑,有效的解决了力学拉伸曲线紊乱,不能准确测定高强贝氏体钢非比例延伸强度RP0.2的问题。     

低碳贝氏体钢中的时效析出行为

测定了Cu-Nb-Cr-Mo系低碳贝氏体钢的时效硬度变化行为,在Gleeble-1500热模拟试验机上模拟了各钢种的蠕变行为,利用金相显微镜、TEM研究了不同钢种的微观组织与沉淀析出.结果表明,含铜钢在不同温度时效时会发生明显的时效硬化效应,在不同温度的蠕变曲线上会出现平台,平台现象是由于蠕变过程中出现了第二相析出,平台出现意味着开始了第二相析出,平台结束则析出过程结束.     

铸态球墨铸铁型内孕育的研究

本文通过最优试验,研究了不同复合孕育剂对球铁型内孕育的影响。结果表明含钡的复合孕育剂有最好的孕育效果;并进一步应用旋转组合设计,获得了球铁型内孕育的机械性能的数学模型,从而得出最优工艺条件。     

恒电位脉冲法检测高纯铁素体不锈钢的敏化

用恒电位脉冲（ＰＰＴ）法对高纯铁素体不锈钢的敏化度进行了检测，并与传统的动电位再活化（ＥＰＲ）法进行了比较，结果表明：ＰＰＴ法可以用来检测铁素体不锈钢的敏化，并且具有检测速度快，表面损伤小的优点     

冷轧工艺对铁素体不锈钢成形性能的影响

为了研究冷轧工艺对新型铁素体不锈钢19Cr2Mo1W成形性能的影响,采用XRD,EBSD技术以及平均塑性应变比与粗糙度测量等手段,研究了不同压下率冷轧及随后退火过程中的织构演变和微观组织变化,并讨论了织构和微观组织对成形性能的影响.结果表明:随着冷轧压下率的增加,铁素体不锈钢中的α和γ纤维织构均有所增强,且α和γ纤维织构最终稳定取向分别为223〈110〉和111〈011〉.冷轧板α纤维织构中223〈110〉组分越强,退火后γ再结晶织构强度越高.冷轧板在1050℃退火时,薄板的γ再结晶织构强度高,再结晶组织均匀且尺寸较小,表面粗糙度最小,综合成形性能最佳.     

超纯Cr17铁素体不锈钢热变形过程的动态回复行为

采用热力模拟试验机进行单道次压缩试验,旨在揭示超纯Cr17铁素体不锈钢在热变形过程中的动态回复行为.在变形速率为1 s-1,最大真应变为0.8的条件下研究了900~1 150℃范围内的热变形行为及组织演化规律.结果表明,单道次压缩得到的应力-应变曲线均呈动态回复型.变形温度越高,动态回复越快.当变形温度较低时,微观组织演化以晶界拱出和变形晶粒的形成为主要特征;当变形温度较高时,微观组织演化以大量亚晶界和亚晶的形成为主要特征.     

盐酸浓度对热轧不锈钢酸洗板表面质量的影响

借助电化学方法、激光共聚焦显微镜和SEM等分析手段,研究了盐酸浓度对热轧铁素体不锈钢表面质量的影响作用.结果表明:在本实验条件下,随着盐酸浓度的增加,酸洗后不锈钢表面平整程度增加,但盐酸浓度过高存在较严重的晶间腐蚀现象.虽然酸洗后不锈钢的阴阳极极化曲线形状在弱极化区并没有发生太大的变化,但随着盐酸浓度的增加,不锈钢在溶液中的点蚀电位升高,并且容抗弧半径增大,表面耐蚀性增强.     

Effect of tin addition on the microstructure and properties of ferritic stainless steel

This article reports the effects of Sn on the inclusions as well as the mechanical properties and hot workability of ferritic stainless steel. Precipitation phases and inclusions in Sn-bearing ferritic stainless steel were observed, and the relationship between the workability and the microstructure of the steel was established. Energy-dispersive X-ray spectroscopic analysis of the steel reveals that an almost pure Sn phase forms and MnS-Sn compound inclusions appear in the steel with a higher Sn content. Little Sn segregation was observed in grain boundaries and in the areas around sulfide inclusions; however, the presence of Sn does not adversely affect the workability of the steel containing 0.4wt% Sn. When the Sn content is 0.1wt%-0.4wt%, Sn improves the tensile strength and the plastic strain ratio and also improves the plasticity with increasing temperature. A mechanism of improving the workability of ferritic stainless steel induced by Sn addition was discussed:the presence of Sn lowers the defect concentration in the ultra-pure ferritic lattice and the good distribution of tin in the lattice overcomes the problem of hot brittleness that occurs in low-carbon steel as a result of Sn segregation.     

Microstructure, crystallography and nucleation mechanism of NANOBAIN steel

The microstructure of bainite ferrite in NANOBAIN steel transformed at different temperatures was investigated by scanning electron microscopy, transmission electron microscopy, electron back-scattered diffraction, and vickers hardness tester in detail. It is found that the average width of bainitic ferrite (BF) plates can be refined to be thinner with the reduction of temperature (473–573 K), and the bainitic ferrite plates can reach up to 20–74 nm at 473 K. Crystallographic analysis reveals that the bainitic ferrite laths are close to the Nishiyama-Wasserman orientation relationship with their parent austenite. Temperature shows a significant effect on the variant selection, and a decrease in temperature generally weakens the variant selection. Thermodynamic analyses indicates that the Lacher, Fowler and Guggenheim (LFG) model is more suitable than the Kaufman, Radcliffe and Cohen (KRC) model dealing with NANOBAIN steel at a low temperature range. The free energy change ΔGγ→BF is about ?1500 J·mol?1 at 473 K, which indicates that nucleation in NANOBAIN steel is the shear mechanism. Finally, the formation of carbon poor regions is thermodynamically possible, and the existence of carbon poor regions can greatly increase the possibility of the shear mechanism.