铸造高合金不锈钢析出相及腐蚀行为的研究

采用金相显微镜、Ｘ射线衍射，透射电镜，电子探针显微分析手段和多种腐蚀试验方法研究了铸造高合金不锈钢的析出相种类，结构、形貌，分布，成分及基腐蚀行为。试验结果表明，该钢经１１５０℃×２ｈ冷固溶处理后可得到单一的奥氏体组织，并具有优良的均匀腐蚀，晶间腐蚀、点蚀与电化学腐蚀性能。     

低碳钢中纳米尺寸碳化物的相间析出行为

采用扫描电镜和透射电子显微镜对低碳Ti-Mo系的热轧板进行了组织分析,同时对其中的纳米粒子析出行为进行了研究.强化机理分析表明析出强化对于屈服强度的贡献值可达291 MPa.随着卷取温度的降低,纳米粒子相间析出的排间距会减小,相间析出的排间距与其在铁素体中形核点位置有一定的离散值,但基本上呈一定的固定值.α/γ界面的观察和采用不同理论的计算结果表明相间析出的产生主要与α/γ界面的台阶形成有关,相间析出的排间距大小由台阶高度、晶界扩散系数、等温温度、台阶面迁移速率等决定.     

高强度低合金钢的微合金在热轧过程中的析出动力学

高强度低合金钢（ＨＳＬＡ）在热轧过程微合金元素（Ｎｂ－Ｔｉ－Ｖ）的析出，对确保ＨＳＬＡ钢机械性能的再现性和均匀性十分重要。本文就热轧中工艺参数和钢的化学成分对析出动力的影响，利用局部电解法（ＳＥＤ）进行了定量的研究。对热轧中工艺参数和钢的化学成分对析出动务的，利用局部电解法（ＳＥＤ）进行了定量的研究。对热轧过程中在奥氏体中与在铁素体中的非等和等温析出动力进行了比较和研究。相变期间或相变之后的重要差     

高强度热轧耐候钢的钒析出行为与时效性能研究

结合攀枝花现有的资源特点,针对性地进行含V高强度耐候钢研究。采用热模拟试验、相分析、拉伸试验等方法,研究了不同工艺条件下钒氮微合金化高强耐候钢的V析出行为及时效性能。研究表明:随N含量的增加,不同温度卷取的试验钢中V的析出比例明显高于对比钢,增N后V析出量明显增加,并且在冷却过程中V析出趋势增加;随V/N值的升高,AI值降低,当V/N低于3.5时对时效性能不利。通过研究,确定了450 MPa级高强度耐候钢关键控制参数,考虑晶粒细化和沉淀强化的综合作用,试验钢的最佳卷取温度为650℃;考虑到N对时效指数的影响,钒氮微合金化高强耐候钢中的V/N值控制略高于V与N理想化学配位数(3.64),试验钢的综合性能较佳。     

油气工业中氢对双相不锈钢腐蚀行为的影响

随着双相不锈钢在海洋油气田和酸性服役工况下的应用越来越多,临氢环境下双相不锈钢的失效风险逐步提高.目前海洋油气田双相不锈钢管道面临的氢损伤失效主要出现在海水过阴极保护环境和含H₂S的酸性服役环境.氢的引入除了引起双相不锈钢腐蚀性能和组织的改变外,还不可避免遭受氢损伤,包括氢脆、氢致开裂等.本文综述了氢进入双相不锈钢后引起的氢损伤问题、腐蚀性能的改变和组织的改变,旨在为双相不锈钢油气工业临氢环境下的应用提供指导;总结了氢在双相不锈钢中扩散和分布的研究现状：氢在双相不锈钢中的扩散路径是曲折的,倾向于在晶界处聚集,随后向铁素体扩散;介绍了与氢相关的现代分析技术与方法,同时展望了临氢环境双相不锈钢研究的发展趋势：氢损伤理论机制仍不完善,需要将现代分析技术和理论计算模拟相结合完善和发展新的氢损伤理论模型.     

铌微合金化HSLA钢铁素体中Nb(C,N)析出强化的研究进展

介绍了含微量铌的高强度低合金(HSLA)钢铁素体中Nb(C,N)析出的数学模型,以及计算经900～1200℃奥氏体化处理后的铁素体中NbC形核半径、形核率和形核长大率。一些研究者的试验结果表明,Nb的碳氮化物在铁素体上的析出需要较高的位错密度,与奥氏体中形成的NbC相比较,铁素体中形成的NbC相对较少,在680℃卷取钢板的抗拉强度较未经卷取直接空冷至室温的钢板抗拉强度有明显提高。     

Titanium nitride precipitation behavior in thin-slab cast high-strength low-alloy steels

To assess the potential for obtaining and utilizing titanium nitride (TiN) refinement via the increased postsolidification cooling rates associated with thin-slab casting, TiN particle size distributions were evaluated by transmission electron microscope (TEM) examination of carbon extraction replicas. Eight commercially produced thin-slab cast TiN steels, nominally 0.05 pct C, 1.2 pct Mn, and one conventionally cast steel were received. Thin slab samples were taken from three locations in the production process: quenched after casting before the tunnel furnace, quenched after tunnel furnace soaking, and the as-rolled and air-cooled final product. Effects of cooling rate were evident in the results and agree with previously documented behavior, where precipitate size decreases with increased cooling rate. Statistical differences in particle size between specimens from steels with different chemistries were shown. These variations result from differences in the driving force for precipitation, rates of coarsening, and differences in volume fraction due to changes in steel composition. The interaction of composition and processing, such as soaking in the tunnel furnace and rolling, was found to be important. For example, the hyperstoichiometric steel (excess Ti) exhibited fine TiN after casting and soaking, but dramatic coarsening after hot rolling. This behavior was attributed to deformation enhanced particle coarsening, or incomplete precipitation after soaking, followed by continued growth during subsequent processing.     

Influence of alloying elements on the kinetics of strain-induced martensitic nucleation in low-alloy, multiphase high-strength steels

Low-alloy multiphase transformation-induced-plasticity (TRIP) steels offer excellent mechanical properties in terms of elongation and strength. This results from the complex synergy between the different phases, i.e., ferrite, bainite, and retained austenite. The precise knowledge of the austenite-to-martensite transformation kinetics is required to understand the behavior of TRIP steels in a wide array of applications. The parameters determining the stability of the metastable austenite were reviewed and investigated experimentally, with special attention paid to the effect of the chemical composition, the temperature, and the size of the austenite particles. The results show that the stability and rate of transformation of the austenite particles in TRIP steels have a pronounced composition dependence: austenite particles transform at a faster rate in CMnSi TRIP steel than in TRIP steels in which Si is fully or partially replaced by Al and P. The results clearly support the view that (1) both a high C content and a submicron size are required for the room-temperature stability of the austenite particles and (2) the effect of the chemical composition on the transformation is due to its influence on the intrinsic stacking-fault energy. In addition, the composition dependence of the Md ₃₀ temperature was derived by regression analysis of experimental data. The influence of the size of the retained austenite particles on their Ms ^σ temperature was studied by means of a thermodynamic model. Both the analysis of the transformation-kinetics data and the microstructural analysis by transmission electron microscopy revealed the very limited role of autocatalysis in the transformation.     

Coarsening kinetics of multicomponent MC-type carbides in high-strength low-alloy steels

Morphology and coarsening kinetics of MC-type carbide (MC-carbide) precipitating during the tempering process have been investigated in V- and Nb-bearing Cr-Mo martensitic steels. Detailed transmission electron microscopy (TEM) observations show that the addition of V and Nb stabilizes the B1-type MC-carbide instead of L’3-type M₂C-carbide. The morphology of the MC-carbide is characterized as disk-like with Baker and Nutting orientation relationships with the matrix. When the specimens are fully solution treated followed by quenching, the MC-carbide precipitates as a multicomponent system with continuous solid solution of VC, NbC, and MoC. The V-, Nb-, and Mo-partitioning control the lattice parameter of MC-carbide and consequently affect the coherency between MC-carbide and the matrix. The coherent MC-carbide grows into an incoherent one with the progress of tempering. The numerical analysis on TEM observations has shown that the coarsening kinetics of MC-carbide is equated to (time)^1/5 criteria, while the coarsening kinetics of the coexisting cementite is equated to (time)^1/3 criteria. It is thus suggested that the Ostwald ripening of MC-carbide is controlled by pipe diffusion of V, Nb, and Mo along dislocations. It has been confirmed that the coarsening rate of the multicomponent MC-carbide is affected by V, Nb, and Mo content. Applying the thermodynamic solution database, the rate equation for MC-carbide coarsening can be expressed as a function of V, Nb, and Mo content, and the activation energy for pipe diffusion can be estimated as ΔQ _v: ΔQ _Nb: ΔQ _Mo=1:3.9:0.6.     

Strain-aging of vanadium,niobium or titanium-strengthened high-strength low-alloy steels

Four commercially available high-strength low-alloy (HSLA) steels were evaluated in this study. It was determined that all four steels were susceptible to strain-aging by interstitial solutes. The increase in strength due to strain-aging was similar to that observed in a low carbon steel studied for comparison. At high levels of prestrain, the percent loss in ductility in the HSLA steels was comparable to that observed in the low-carbon steel in specimens prestrained to the same fraction of the total elongation of the as-received metal. However, when considered on an absolute basis, the residual ductility in the HSLA steels was 25 to 50 pct of that observed in the low-carbon steel. The kinetics of strain-aging were briefly examined. Indications are that the kinetics are slower in the HSLA steels than they are in the low-carbon steel.     

Strain-aging of vanadium, niobium or titanium-strengthened high-strength low-alloy steels

Four commercially available high-strength low-alloy (HSLA) steels were evaluated in this study. It was determined that all four steels were susceptible to strain-aging by interstitial solutes. The increase in strength due to strain-aging was similar to that observed in a low carbon steel studied for comparison. At high levels of prestrain, the percent loss in ductility in the HSLA steels was comparable to that observed in the low-carbon steel in specimens prestrained to the same fraction of the total elongation of the as-received metal. However, when considered on an absolute basis, the residual ductility in the HSLA steels was 25 to 50 pct of that observed in the low-carbon steel. The kinetics of strain-aging were briefly examined. Indications are that the kinetics are slower in the HSLA steels than they are in the low-carbon steel.