Abrasive resistance of metastable V–Cr–Mn–Ni spheroidal carbide cast irons using the factorial design method

Full factorial design was used to evaluate the two-body abrasive resistance of 3wt%C–4wt%Mn–1.5wt%Ni spheroidal carbide cast irons with varying vanadium (5.0wt%–10.0wt%) and chromium (up to 9.0wt%) contents. The alloys were quenched at 920℃. The regression equation of wear rate as a function of V and Cr contents was proposed. This regression equation shows that the wear rate decreases with increasing V content because of the growth of spheroidal VC carbide amount. Cr influences the overall response in a complex manner both by reducing the wear rate owing to eutectic carbides (M₇C₃) and by increasing the wear rate though stabilizing austenite to deformation-induced martensite transformation. This transformation is recognized as an important factor in increasing the abrasive response of the alloys. By analyzing the regression equation, the optimal content ranges are found to be 7.5wt%–10.0wt% for V and 2.5wt%–4.5wt% for Cr, which corresponds to the alloys containing 9vol%–15vol% spheroidal VC carbides, 8vol%–16vol% M₇C₃, and a metastable austenite/martensite matrix. The wear resistance is 1.9–2.3 times that of the traditional 12wt% V–13wt% Mn spheroidal carbide cast iron.     

异面直线公垂线的投影阵

讨论异面直线的一个投影阵公式,并由此得出异面直线的距离公式为d= | (M₁- M₂ M₂- M₁
M₂- M₁) (X ₁- M₂
X ₂- M₁
M₂- M₁)^{- 1}(X ₁- X ₂) | .     

三角矩阵环上的(n,d)-内射模

设A,B是环,U是(B,A)-双模,n,d为非负整数,T=(A 0U B)是形式三角矩阵环,首先,证明了M=(M₁M₂)_φ^M是n-表现左T-模当且仅当M₁是n-表现左A-模,Coker φ^M是n-表现左B-模且φ^M:U_AM₁ → M₂是单同态。其次,证明了当M=(M₁M₂)_φ^M是(n,d)-内射左T-模时,M₁是(n,d)-内射左A-模,M₂是(n,d)-内射左B-模。     

形式三角矩阵环上的n-Gorenstein投射模

设n是整数,T=(A 0U B)是形式三角矩阵环,其中A,B是环,U是左B右A双模,_BU是投射模,U_A的平坦维数有限。证明了若左T-模(M₁M₂)_φ^M是n-Gorenstein投射模,则M₁是(n-1)-Gorenstein投射左A-模,M₂/Im(φ^M)是n-Gorenstein投射左B-模,并且 φ^M:U⊗_AM₁→M₂是单射。反过来,若M₁是n-Gorenstein投射左A-模,M₂/Im(φ^M)是n-Gorenstein投射左B-模,并且 φ^M:U⊗_AM₁→M₂是单射,则左T-模(M₁M₂)_φ^M是n-Gorenstein投射模。     

航空轴承钢渗碳热处理组织演变行为研究

利用EPMA与XRD等实验方法对航空轴承钢在渗碳热处理过程中的微观组织演变行为进行定性及定量分析.结果表明:在渗碳淬火处理后,试样表层及次表层组织中有大量的碳化物及少量的残留奥氏体,其中碳化物为M₂₃C₆和M₆C.随着渗层深度的增加,碳化物含量减少,残留奥氏体含量增加.经过二次淬火处理后,奥氏体与马氏体中碳质量分数增加,使得淬火后残留奥氏体质量分数大幅度增加,在渗层0.1mm处达到22.7%.经过两次深冷与回火处理后,马氏体与奥氏体中碳质量分数降低,碳化物含量增加,渗层硬度提升.     

三角矩阵环上投射余可解的Gorenstein平坦模

设T=((A 0 U B))是三角矩阵环, 其中A和B是环, U是(B,A)-双模. 用环T上模张量的同构式作为桥梁, 给出环T上的模是投射余可解的Gorenstein平坦模的等价条件: 若fd(_BU)<∞, fd(U_A)<∞或id(U_A)<∞, 则左T-模M=((M₁ M₂))_φ^M是投射余可解的Gorenstein平坦模当且仅当M₁是投射余可解的Gorenstein平坦左A-模,  Coker φ^M=M₂/Im(φ^M)是投射余可解的Gorenstein平坦左B-模, 且φ^M: U*_AM₁→M₂是单同态.     

铈镍合金的“氢通道”和“氢溢出”效应协同改善氢化镁的储氢性能

氢化镁（MgH₂）因其储氢容量高(7.6wt%)、资源丰富、可逆性好等优势而在能源材料的开发方面得到了越来越多的关注。然而,MgH₂较强的金属–氢键导致其吸放氢反应动力学缓慢、热力学稳定性过高,难以获得广泛的实际应用。本文成功设计并合成了CeNi₅合金,有效改善了MgH₂的储氢性能。研究结果表明,氢化以及湿化学球磨处理后的CeNi₅ 合金呈现片层状结构,MgH₂–CeNi₅复合材料中CeNi₅含量的增加可以有效地降低MgH₂的起始放氢温度。 MgH₂–5wt%CeNi₅复合材料的初始放氢温度为174°C,比纯MgH₂的放氢温度降低了156°C。复合体系在275℃的温度下,10分钟内释放出约6.4wt%的H₂。此外,完全脱氢的样品在175℃的低温下吸收了4.8wt%的H₂,并且吸氢过程的表观活化能从(73.60 ± 1.79)下降到(46.12 ± 7.33) kJ/mol。微观结构分析表明,原位生成的Mg₂Ni/Mg₂NiH₄和CeH_2.73分别展现出“氢通道”和 “氢溢流”效应,从而有效增强了MgH₂–5wt%CeNi₅复合材料的储氢性能。     

Fabrication of Fe–TiC–Al2O3 composites on the surface of steel using a TiO2–Al–C–Fe combustion reaction induced by gas tungsten arc cladding

The aim of the present study was to fabricate Fe–TiC–Al₂O₃ composites on the surface of medium carbon steel. For this purpose, TiO₂–3C and 3TiO₂–4Al–3C–xFe (0 ≤ x ≤ 4.6 by mole) mixtures were pre-placed on the surface of a medium carbon steel plate. The mixtures and substrate were then melted using a gas tungsten arc cladding process. The results show that the martensite forms in the layer produced by the TiO₂–3C mixture. However, ferrite–Fe₃C–TiC phases are the main phases in the microstructure of the clad layer produced by the 3TiO₂–4Al–3C mixture. The addition of Fe to the TiO₂–4Al–3C reactants with the content from 0 to 20wt% increases the volume fraction of particles, and a composite containing approximately 9vol% TiC and Al₂O₃ particles forms. This composite substantially improves the substrate hardness. The mechanism by which Fe particles enhance the TiC + Al₂O₃ volume fraction in the composite is determined.     

不同结构和形态的天然镁硅酸盐:与K反应制备生物柴油的K2MgSiO4催化剂

In this work, different magnesium silicate mineral samples based on antigorite, lizardite, chrysotile (which have the same general formula Mg₃Si₂O₅(OH)₄), and talc (Mg₃Si₄O₁₀(OH)₂) were reacted with KOH to prepare catalysts for biodiesel production. Simple impregnation with 20wt% K and treatment at 700–900°C led to a solid-state reaction to mainly form the K₂MgSiO₄ phase in all samples. These results indicate that the K ion can diffuse into the different Mg silicate structures and textures, likely through intercalation in the interlayer space of the different mineral samples followed by dehydroxylation and K₂MgSiO₄ formation. All the materials showed catalytic activity for the transesterification of soybean oil (1:6 of oil : methanol molar ratio, 5wt% of catalyst, 60°C). However, the best results were obtained for the antigorite and chrysotile precursors, which are discussed in terms of mineral structure and the more efficient formation of the active phase K₂MgSiO₄.     

Primary beneficiation of tantalite using magnetic separation and acid leaching

Primary beneficiation was successfully performed prior to dissolution of manganotantalite (sample A) and ferrotantalite (sample C) samples obtained from two different mines in the Naquissupa area, Mozambique. Magnetic separation removed the majority of iron and titanium, whereas H₂SO₄ leaching removed a large portion of thorium and uranium in these samples. Analytical results indicated that 64.14wt% and 72.04wt% of the total Fe and Ti, respectively, and ~2wt% each of Nb₂O₅ and Ta₂O₅ were removed from sample C (ferrotantalite) using the magnetic separation method, whereas only 9.64wt% and 8.66wt% of total Fe₂O₃ and TiO₂, respectively, and ~2wt% each of Nb₂O₅ and Ta₂O₅ were removed from sample A (manganotantalite). A temperature of 50°C and a leaching time of 3 h in the presence of concentrated H₂SO₄ were observed to be the most appropriate leaching conditions for removal of radioactive elements from the tantalite ores. The results obtained for sample A under these conditions indicated that 64.14wt% U₃O₈ and 60.77wt% ThO₂ were leached into the acidic solution, along with 4.45wt% and 0.99wt% of Nb₂O₅ and Ta₂O₅, respectively.     

Sintering behaviors and consolidation mechanism of high-chromium vanadium and titanium magnetite fines

To achieve high efficiency utilization of high-chromium vanadium–titanium magnetite (V–Ti–Cr) fines, an investigation of V–Ti–Cr fines was conducted using a sinter pot. The chemical composition, particle parameters, and granulation of V–Ti–Cr mixtures were analyzed, and the effects of sintering parameters on the sintering behaviors were investigated. The results indicated that the optimum quicklime dosage, mixture moisture, wetting time, and granulation time for V–Ti–Cr fines are 5wt%, 7.5wt%, 10 min, and 5–8 min, respectively. Meanwhile, the vertical sintering speed, yield, tumbler strength, and productivity gains were shown to be 21.28 mm/min, 60.50wt%, 58.26wt%, and 1.36 t·m-2·h-1, respectively. Furthermore, the consolidation mechanism of V–Ti–Cr fines was clarified, revealing that the consolidation of a V–Ti–Cr sinter requires an approximately 14vol% calcium ferrite liquid-state, an approximately 15vol% silicate liquid-state, a solid-state reaction, and the recrystallization of magnetite. Compared to an ordinary sinter, calcium ferrite content in a V–Ti–Cr sinter is lower, while the perovskite content is higher, possibly resulting in unsatisfactory sinter outcomes.     

Microstructural evolution and castability prediction in newly designed modern third-generation nickel-based superalloys

The present research aims to establish a quantitative relation between microstructure and chemical composition (i.e., Ti, Al, and Nb) of newly designed nickel-based superalloys. This research attempts to identify an optimum microstructure at which the minimum quantities of γ/γ' and γ/γ″ compounds are achieved and the best castability is predicted. The results demonstrate that the highest quantity of intermetallic eutectics (i.e., 41.5wt%) is formed at 9.8wt% (Ti + Al). A significant quantity of intermetallics formed in superalloy 1 (with a composition of γ-9.8wt% (Ti + Al)), which can deteriorate its castability. The type and morphology of the eutectics changed and the amount considerably decreased with decreasing Ti + Al content in superalloy 2 (with a composition of γ-7.6wt% (Ti + Al), 1.5wt% Nb). Thus, it is predicted that the castability would improve for superalloy 2. The same trend was observed for superalloy 4 (with a composition of γ-3.7wt% (Ti + Al), 4.4wt% Nb). This means that the amount of Laves increases with increasing Nb (to 4.4wt%) and decreasing Ti + Al (to 3.7wt%) in superalloy 4. The best castability was predicted for superalloy 3 (with a composition of γ-5.7wt% (Ti + Al), 2.8wt% Nb).     

Effect of initial microstructure on austenite formation kinetics in high-strength experimental microalloyed steels

Austenite formation kinetics in two high-strength experimental microalloyed steels with different initial microstructures compris-ing bainite–martensite and ferrite–martensite/austenite microconstituents was studied during continuous heating by dilatometric analysis. Austenite formation occurred in two steps:(1) carbide dissolution and precipitation and (2) transformation of residual ferrite to austenite. Di-latometric analysis was used to determine the critical temperatures of austenite formation and continuous heating transformation diagrams for heating rates ranging from 0.03°C×s?1 to 0.67°C×s?1. The austenite volume fraction was fitted using the Johnson–Mehl–Avrami–Kolmogorov equation to determine the kinetic parameters k and n as functions of the heating rate. Both n and k parameters increased with increasing heat-ing rate, which suggests an increase in the nucleation and growth rates of austenite. The activation energy of austenite formation was deter-mined by the Kissinger method. Two activation energies were associated with each of the two austenite formation steps. In the first step, the austenite growth rate was controlled by carbon diffusion from carbide dissolution and precipitation;in the second step, it was controlled by the dissolution of residual ferrite to austenite.     

In situ observation of austenite grain growth behavior in the simulated coarse-grained heat-affected zone of Ti-microalloyed steels

The austenite grain growth behavior in a simulated coarse-grained heat-affected zone during thermal cycling was investigated via in situ observation. Austenite grains nucleated at ferrite grain boundaries and then grew in different directions through movement of grain boundaries into the ferrite phase. Subsequently, the adjacent austenite grains impinged against each other during the α→γ transformation. After the α→γ transformation, austenite grains coarsened via the coalescence of small grains and via boundary migration between grains. The growth process of austenite grains was a continuous process during heating, isothermal holding, and cooling in simulated thermal cycling. Abundant finely dispersed nanoscale TiN particles in a steel specimen containing 0.012wt% Ti effectively retarded the grain boundary migration, which resulted in refined austenite grains. When the Ti concentration in the steel was increased, the number of TiN particles decreased and their size coarsened. The big particles were not effective in pinning the austenite grain boundary movement and resulted in coarse austenite grains.     

Kinetics and formation mechanisms of intragranular ferrite in V-N microalloyed 600 MPa high strength rebar steel

To systematically investigate the kinetics and formation mechanisms of intragranular ferrite (IGF), isothermal heat treatment in the temperature range of 450℃ to 600℃ with holding for 30 s to 300 s, analysis of the corresponding microstructures, and observation of the precipitated particles were conducted in V-N microalloyed 600 MPa high strength rebar steel. The potency of V(C,N) for IGF nucleation was also analyzed statistically. The results show that the dominant microstructure transforms from bainite (B) and acicular ferrite (AF) to grain boundary ferrite (GBF), intragranular polygonal ferrite (IPF), and pearlite (P) as the isothermal temperature increases from 450℃ to 600℃. When the holding time at 600℃ is extended from 30 s to 60 s, 120 s, and 300 s, the GBF content ranges from 6.0vol% to 6.5vol% and the IPF content increases from 0.5vol% to 2.8vol%, 13.1vol%, and 13.5vol%, respectively, because the ferrite transformation preferentially occurs at the grain boundaries and then occurs at the austenite grains. Notably, V(C,N) particles are the most effective nucleation site for the formation of IPF, accounting for 51% of the said formation.     

Thermal and microstructural characterization of a novel ductile cast iron modified by aluminum addition

In high-temperature applications, like exhaust manifolds, cast irons with a ferritic matrix are mostly used. However, the increasing demand for higher-temperature applications has led manufacturers to use additional expensive materials such as stainless steels and Ni-resist austenitic ductile cast irons. Thus, in order to meet the demand while using low-cost materials, new alloys with improved high-temperature strength and oxidation resistance must be developed. In this study, thermodynamic calculations with Thermo-Calc software were applied to study a novel ductile cast iron with a composition of 3.5 wt% C, 4 wt% Si, 1 wt% Nb, 0-4 wt% Al. The designed compositions were cast, and thermal analysis and microstructural characterization were performed to validate the calculations. The lowest critical temperature of austenite to pearlite eutectoid transformation, i.e., A1, was calculated, and the solidification sequence was determined. Both calculations and experimental data revealed the importance of aluminum addition, as the A1 increased by increasing the aluminum content in the alloys, indicating the possibility of utilizing the alloys at higher temperature. The experimental data validated the transformation temperature during solidification and at the solid state and confirmed the equilibrium phases at room temperature as ferrite, graphite, and MC-type carbides.     

分段冷却模式下热轧双相钢的组织演变及力学性能

通过热模拟实验研究了分段冷却模式下变形温度、保温温度及保温时间对Nb-Ti微合金热轧双相钢组织演变及性能的影响.结果表明:降低变形温度可促进铁素体的转变,使马氏体形态由大块状过渡到岛状;保温温度从740℃逐渐降至580℃时,铁素体转变量先增加后减少,保温温度为660℃时铁素体转变量达到峰值;随保温时间延长铁素体转变量增加,且铁素体转变量与时间的关系曲线呈“S”型.采用超快冷+空冷+层流冷的冷却模式并通过调整终轧温度及空冷时间获得了630~710MPa的热轧双相钢,屈强比≤061,相应的组织为铁素体+马氏体或铁素体+马氏体+少量的贝氏体.     

Mechanical properties and characteristics of nanometer-sized precipitates in hot-rolled low-carbon ferritic steel

The microstructures and properties of hot-rolled low-carbon ferritic steel have been investigated by optical microscopy, field-emission scanning electron microscopy, transmission electron microscopy, and tensile tests after isothermal transformation from 600℃ to 700℃ for 60 min. It is found that the strength of the steel decreases with the increment of isothermal temperature, whereas the hole expansion ratio and the fraction of high-angle grain boundaries increase. A large amount of nanometer-sized carbides were homogeneously distributed throughout the material, and fine (Ti, Mo)C precipitates have a significant precipitation strengthening effect on the ferrite phase because of their high density. The nanometer-sized carbides have a lattice parameter of 0.411–0.431 nm. After isothermal transformation at 650℃ for 60 min, the ferrite phase can be strengthened above 300 MPa by precipitation strengthening according to the Ashby-Orowan mechanism.