Dynamic recrystallization behavior of Fe–20Cr–30Ni–0.6Nb–2Al–Mo alloy

Single-pass compression tests of an aluminaforming austenite(AFA) alloy(Fe–20Cr–30Ni–0.6Nb–2Al–Mo) were performed using a Gleeble-3500 thermal–mechanical simulator. By combining techniques of electron back-scattered diffraction(EBSD) and transmission electron microscopy(TEM), the dynamic recrystallization(DRX) behavior of the alloy at temperatures of 950–1100 ℃ and strain rates of 0.01–1.00 s~(-1) was investigated. The regression method was adopted to determine the thermal deformation activation energy and apparent stress index and to construct a thermal deformation constitutive model. Results reveal that the flow stress is strongly dependent on temperature and strain rate and it increases with temperature decreasing and strain rate increasing. The DRX phenomenon occurs more easily at comparably higher deformation temperatures and lower strain rates. Based on the method for solving the inflection point via cubic polynomial fitting of strain hardening rate(h) versus strain(e) curves, the ratio of critical strain(ec) to peak strain(ep) during DRX was precisely predicted. The nucleation mechanisms of DRX during thermal deformation mainly include the strain-induced grain boundary(GB)migration, grain fragmentation, and subgrain coalescence.     

Accelerated precipitation in the AFA stainless steel Fe–20Cr–30Ni–2Nb–5Al via cold working

The effects of cold work on the microstructural evolution during aging of a solutionized alumina-forming austenitic stainless steel, Fe–20Cr–30Ni–2Nb–5Al (at.%), were investigated using scanning electron microscopy, transmission electron microscopy, and scanning transmission electron microscopy. Cold work prior to aging at either 700 °C or 800 °C facilitated the heterogeneous precipitation of both Laves phase and B2-type NiAl precipitates. While often co-located after cold work, these particles were distinct. γ′-Ni₃Al precipitates were also observed in samples aged at 700 °C with 90% prior cold work. Compared to material that had not been strained, defects introduced by 50 and 90% cold work at 700 °C and 90% cold work at 800 °C not only caused a more rapid precipitation in the matrix but also an increase in the total volume fraction of precipitates as compared to material that had been simply aged.     

Shape Memory Effect Induced by Stress-induced α' Martensite in a Metastable Fe–Cr–Ni Austenitic Stainless Steel

It is not clear whether a shape memory effect(SME) can be realized by stress-induced α' martensite in metastable austenitic stainless steels although the stress-induced ε martensite in these materials can result in the SME. To clarify this problem, the relationship between the shape recovery and the reverse transformation of the stress-induced ε and α' martensite in a 304 stainless steel was investigated. The results show that the stress-induced α' martensite can result in the SME when heating above 773 K. After deformation at 77 K and step heating or directly holding at 1073 K, two-stage shape recoveries below 440 K and above 773 K can be obtained due to the reverse transformation of the stress-induced e martensite and α' martensite, respectively. After deformation at room temperature, the α' martensite produced can result in the SME only when directly holding at 1073 K. The intrusion of more dislocations before the formation of the α' martensite at room temperature than at 77 K is the reason that the α' martensite induced at room temperature cannot result in the SME in the case of slow heating. The recovered strains resulting from the stress-induced ε and α' martensite are proportional to the amounts of their reverse transformation, respectively.     

Formation and Evolution of Microstructures in Fe–9%Cr Heat-Resistant Steel

Microstructures of casting samples of Fe–9%Cr steel and samples subjected to different heat treatments were investigated to determine their formation and evolution mechanism. The results show that there is no macroscopic segregation in the casting Fe–9%Cr steel. During cooling from solidification temperature to room temperature, d-ferrite→austenite transformation is obviously influenced by cooling rate, while subsequent transformation of austenite does not obviously depend on the cooling rate. In the casting samples, a great number of precipitates distribute inside martensitic laths while there are almost no precipitates inside d-ferrite. When the casting samples were reheated to and isothermally held at 800 °C, the original precipitates and the lath boundaries disappeared gradually. Meanwhile, new precipitates nucleate and grow at the prior lath boundaries.     

Transformation Behavior and Microstructure in a 40Cr2Ni2MoV Cast Steel

The transformation behavior of a 40Cr2Ni2MoV cast steel manufactured by electroslag remelting (ESR) has been investigated. Compared to a forged steel, the incubation periods for both the pearlite and bainite transformations are shorter, but the transformation times are longer. The austenite is easier to transform into martensite. Optical microscopy and TEM indicated that there were variations in microstructure during the super-cooled austenite transformation. This is attributed to an inhomogeneous austenite, resulting from the segregation of elements during the ESR solidification.     

Hot Deformation Behavior of an Ultra-High-Strength Fe–Ni–Co-Based Maraging Steel

Hot processing behavior of an ultra-high-strength Fe–Ni–Co-based maraging steel was studied in temperature range of 900–1200 °C and strain rate range of 0.001–10 s~(-1). Deformation processing parameters and optimum hot working window were characterized via flow stress analysis, constitutive equation construction, hot processing map calculation and microstructure evolution, respectively. Critical strain value for dynamic recrystallization was determined through theoretical mathematical differential method: the inflection point of θ–σ and -αθ/ασ-σ curves. It was found that the flow stress increased with the decrease in deformation temperature and increase in the strain rate. The power dissipation maps in the strain range of 0.1–0.6 were entirely similar with the tendency of contour lines which implied that strain had no strong effect on the dissipation maps. Nevertheless, the instability maps showed obvious strain sensitivity with increasing strain, which was ascribed to the flow localization and instability. The optimized hot processing window of the experimental steel was obtained as 1100–1200 °C/0.001–1 s~(-1) and 1000–1100 °C/0.001–0.1 s~(-1), with the efficiency range of 20–40%. Owing to high Mo content in the experimental steel, high dynamic activation energy, Q = 439.311 kJ mol~(-1), was achieved, indicating that dynamic recrystallization was difficult to occur in the hot deformation process, which was proved via microstructure analysis under different hot deformation conditions.     

High-temperature Oxidation Behavior of a High Manganese Austenitic Steel Fe–25Mn–3Cr–3Al–0.3C–0.01N

In this paper, a Fe–Mn–Al–C austenitic steel with certain addition of Cr and N alloy was used as experimental material. By using the SETSYS Evolution synchronous differential thermal analysis apparatus, the scanning electron microscope(SEM), the electron microprobe(EPMA) and the X-ray diffraction(XRD), the high-temperature oxidation behavior microstructure and the phase compositions of this steel in air at 600–1,000 °C for 8 h have been studied. The results show that in the whole oxidation temperature range, there are three distinct stages in the mass gain curves at temperature higher than 800 °C and the oxidation process can be divided into two stages at temperature lower than 800 °C.At the earlier stage the gain rate of the weight oxidized in temperature range of 850 °C to 1,000 °C are extremely lower.The oxidation products having different surface microstructures and phase compositions were produced in oxidation reaction at different temperatures. The phase compositions of oxide scale formed at 1,000 °C are composed of Fe and Mn oxide without Cr. However, protective film of Cr oxide with complicated structure can be formed when the oxidation temperature is lower than 800 °C.     

Neutron Diffraction Study of Low-Cycle Fatigue Behavior in an Austenitic–Ferritic Stainless Steel

By performing in situ neutron diffraction experiments on an austenitic–ferritic stainless steel subjected to lowcycle fatigue loading, the deformation heterogeneity of the material at microscopic level has been revealed. Based on the in situ neutron diffraction data collected from a single specimen together with the mechanical properties learned from the ex situ micro-hardness, a correlation has been found. The performance versus diffraction-profile correlation agrees with the cyclic-deformation-induced dislocation evolution characterized by ex situ TEM observation. Moreover, based on the refined neutron diffraction-profile data, evident strain anisotropy is found in the austenite. The high anisotropy in this phase is induced by the increase in dislocation density and hence contributes to the hardening of the steel at the first 10 cycles.Beyond 10 fatigue cycles, the annihilation and the rearrangement of the dislocations in both austenitic and ferritic phases softens the plastically deformed specimen. The study suggests that the evolution of strain anisotropy among the differently oriented grains and micro-strain induced by lattice distortion in the respective phases mostly affect the cyclic-deformationinduced mechanical behavior of the steel at different stages of fatigue cycles. The stress discrepancy between phases is not the dominant mechanism for the deformation of the steel.     

Hot Deformation Behavior and Dynamic Recrystallization Characteristics in a Low-Alloy High-Strength Ni–Cr–Mo–V Steel

This study presented a quantitative investigation of deformation behavior and dynamic recrystallization of low-alloy highstrength Ni–Cr–Mo–V steels during hot deformation.A series of isothermal compression experiments were performed at temperatures ranging from 800 to 1200°C and strain rates from 0.01 to 10 s~(-1)with a height reduction of 60%.A complete Arrhenius constitutive model and processing maps were developed.The results showed that the constitutive model had the ability to predict the flow stress with an average absolute relative error of5.7%.The processing maps constructed at strains of 0.2,0.4,and 0.8 showed that flow instability was prone to occur at higher strain.Dynamic recrystallization tended to take place at higher temperatures(900–1200°C)and lower strain rates(0.01–1 s~(-1)).The critical strain for the onset of dynamic recrystallization was determined,and a kinetics model was developed.The predicted results for recrystallization volume fraction and flow stress were compared with the experimental data,which indicated that the model was accurate and reliable.     

Nanoindentation study on solid solution softening of Fe-rich Fe2Nb Laves phase by Ni in Fe–Nb–Ni ternary alloys

In an attempt to understand the solid solution softening by Ni of an Fe-rich Fe₂Nb Laves phase that is in equilibrium with γ-Fe, we have examined the defect structure in the Laves phase in Fe–Nb–Ni alloys by transmission electron microscopy, and its hardness as a function of orientation and solute (Ni) content by nanoindentation. The binary Fe-rich Laves phase and the ternary Laves phases with lower Ni content (18%) exhibit a featureless morphology with low dislocation density, whereas the ternary Laves phase with higher Ni content (33%) includes basal planar faults extending to several micrometers, producing a local change in the stacking sequence of the three 3⁶-nets (triple layer) of the C14 structure. The hardness of the binary and the ternary Laves phases with 18% Ni in solution is almost constant and independent of orientation, whereas the ternary Laves phase with 33% Ni in solution exhibits a substantial dependence of hardness on orientation and this dependence appears associated with the ease of basal slips evidenced by slip traces around nanoindents. The relative ease in activating basal slip in the presence of a large amount of Ni in solution is thought to be the dominant contributor to the observed solid solution softening.     

Al对Fe-20Cr-35Ni-0.6Nb合金显微组织和抗氧化性的影响

采用增量法研究了不同Al含量(0.5%、1.5%、2.5%,质量分数)的Fe-20Cr-35Ni-0.6Nb含Nb合金在1000 ℃空气条件下的抗氧化。采用SEM、EDS、TEM、拉曼光谱等手段研究了合金的显微组织和氧化膜特性。结果表明,3种含Nb合金组织为单相奥氏体,基体中存在少量弥散分布的NbC沉淀相,氧化前后沉淀相含量和晶粒大小保持不变。添加0.5%和1.5%的Al后,含Nb合金的表面形成多层结构的氧化膜,最外层和第三层为Cr₂O₃,次表层主要为NiCr₂O₄、NiFe₂O₄和Fe₂O₃,最内层为Al₂O₃内氧化层。基体中的NbC析出相和氧化膜中少量Nb的氧化物(Nb₂O₅)加剧了氧化膜的疏松。当Al含量增加到2.5%时,含Nb合金表面形成连续致密的Al₂O₃氧化膜,降低了Fe-20Cr-35Ni-0.6Nb合金的氧化速率,提高了抗氧化性。     

时效工艺对25 Cr-20 Ni-2.5 Al高强耐热钢拉伸和高温压缩性能的影响

通过在25Cr-20Ni耐热钢基体成分中加入质量分数为2.5％Al的方式制备25Cr-20Ni-2.5Al耐热钢,分别采用拉伸和高温压缩试验对其力学性能进行表征分析,研究结果表明:经过36 h时效处理的试样抗拉强度得到明显提升,此时抗拉强度和伸长率分别为803 MPa和27.1％.经过36 h时效处理会减小拉伸断口的韧...     

混合稀土对Cu-30Ni-20Fe-5Al微观组织及流动性的影响

采用真空熔炼制备不同稀土含量的Cu-30Ni-20Fe-5Al合金,研究了稀土含量对铸态Cu-30Ni-20Fe-5Al合金组织和流动性能的影响及内在机制。结果表明,铸态Cu-30Ni-20Fe-5Al合金由α-Cu和NiAl化合物两相组成,NiAl相以不规则环状分布,其不规则环状内外两侧存在较大的Fe元素偏析;加入混合稀土后,随混合稀土含量的增加,铸态合金中NiAl相变为球状、棒状独立存在,晶界处出现富稀土相的析出;当混合稀土含量达到0.78%时,不规则环状NiAl相球化效果最好;在流动性试验中,加入0.78%混合稀土元素与不加混合稀土元素比较,自制螺旋试样长度增加25%,合金的流动性能最好。     

热暴露时间对Cr-9Nb合金组织与性能的影响

研究了Cr-9Nb合金在800℃真空环境下热暴露不同时间后组织与性能的变化。结果表明,随着热暴露时间的延长,合金的显微组织存在一定的粗化现象,致密度在前50h时有一定的增加,之后趋于平稳;维氏硬度变化不大,断裂韧度在热暴露100h后降至6.02MPa·m1/2;屈服强度、抗压强度及塑性应变在热暴露前10h时有一定的增加,之后有一定的下降,其中塑性应变下降较明显,热暴露100h后合金仍有高达1536MPa的屈服强度和2203MPa的抗压强度。     

不同温度时效后Ni-20Cr-18W-1Mo合金晶界偏聚及力学性能研究

采用扫描电镜(SEM)、透射电镜(TEM)、电子探针(EPMA)和高温力学试验机等手段,研究了不同时效温度(200-800 °C)对Ni-20Cr-18W-1Mo高温合金的元素晶界偏聚和力学性能的影响。结果表明,硫、磷元素的晶界偏聚临界时间随时效温度升高而降低;时效温度对元素在晶界和晶内的成分分布有显著的影响;实验合金的抗拉强度和延伸率随时效温度升高而降低。分析发现,硫、磷元素在晶界中的含量随时效温度升高而增大直至两者分别在650和400 °C时达到峰值,是合金在200-600 °C区间内力学性能降低的重要原因。     

Fe-20Mn-7Cr-0.9Mo钢与TWIP钢组织和腐蚀性能的比较研究

目的 重点探究Fe-20Mn-7Cr-0.9Mo钢在中国3块不同油田采出水模拟液中的腐蚀行为,为其在石油管材上的应用提供理论指导。方法 在Fe-25Mn-3Si-3Al TWIP钢中添加Cr和Mo元素,降低Mn元素含量,设计制备Fe-20Mn-7Cr-0.9Mo钢。采用X射线衍射仪(XRD)和透射电子显微镜(TEM)对Fe-20Mn-7Cr-0.9Mo钢的微观组织进行分析。利用电化学工作站测试Fe-20Mn-7Cr-0.9Mo钢在3种油田采出水模拟液中的极化曲线和电化学阻抗谱,并使用扫描电子显微镜(SEM)对腐蚀产物进行微观分析。同时,以相同环境中Fe-25Mn-3Si-3Al TWIP钢的腐蚀行为作为对照。结果 Fe-20Mn-7Cr-0.9Mo钢组织以奥氏体为主,其晶粒中含有大量层错、退火孪晶和高密度位错结构的马氏体。通过分析极化曲线可知,与Fe-25Mn-3Si-3Al TWIP钢相比,Fe-20Mn-7Cr-0.9Mo钢在3种油田采出水模拟液中均发生了钝化,腐蚀电位提高,腐蚀电流密度明显降低,分别为1.7、0.08、2.1 μA/cm²。通过分析电化学阻抗谱可知,Fe-20Mn-7Cr-0.9Mo钢在3种油田采出水模拟液中均呈现单一的电容回路,极化电阻Rp分别为3 111、5 322、3 582 Ω.cm²,而Fe-25Mn-3Si-3Al TWIP钢在3种油田采出水模拟液中呈现1个电容回路和1个电感回路,相应的极化电阻Rp仅为530、273、528 Ω.cm²,远小于Fe-20Mn-7Cr-0.9Mo钢。在3种油田采出水模拟液中,Fe-20Mn-7Cr-0.9Mo钢试样表面仅存在少量腐蚀产物,而Fe-25Mn-3Si-3Al TWIP钢试样表面存在大量的腐蚀产物,并形成了腐蚀产物膜。结论 Cr与Mo元素的添加和Mn元素含量的减少,降低了Fe-20Mn-7Cr-0.9Mo钢的堆垛层错能,导致晶粒中形成了大量层错、退火孪晶和少量马氏体。在3种油田采出水模拟液中,Cr与Mo元素的添加、Mn元素含量的减少和晶粒中退火孪晶的形成有效提高了Fe-20Mn-7Cr-0.9Mo钢的耐蚀性。