准晶增强镁、铝基复合材料的研究进展

综述了利用准晶作为镁、铝合金增强相的研究进展。Mg3Zn6Y准晶的界面能低,与α-Mg基体之间形成稳定的界面结合,在高温变形过程中,准晶本身不发生粗化且可以抑制基体组织演化,因此,Mg3Zn6Y准晶增强变形Mg基复合材料具有中等强度和较高的室温、高温塑性。由于到目前为止发现的Al系稳定准晶都不与Al相共生,准晶增强Al基复合材料主要采用快速凝固的方法和外加的方法制备,如粉末冶金法、机械合金化法和液态搅拌法等。综述了采用以上方法制得的准晶增强Al基复合材料的组织特征及其力学性能。     

Forgeability test of extruded Mg–Sn–Al–Zn alloys under warm forming conditions

Magnesium (Mg) alloys have been thoroughly researched to replace steel or aluminum parts in automotives for reducing weight without sacrificing their strength. The widespread use of Mg alloys has been limited by its insufficient formability, which results from a lack of active slip systems at room temperature. It leads to a hot forming process for Mg alloys to enhance the formability and plastic workability. In addition, forged or formed parts of Mg alloys should have the reliable initial yield and ultimate tensile strength after hot working processes since its material properties should be compatible with other parts thereby guaranteeing structural safety against external load and crash. In this research, an optimal warm forming condition for applying extruded Mg–Sn–Al–Zn (TAZ) Mg alloys into automotive parts is proposed based on T-shape forging tests and the feasibility of forged parts is evaluated by measuring the initial yield strength and investigating the grain size in orientation imaging microscopy (OIM) maps.     

Effects of Zn content on microstructures and mechanical properties of as cast Mg–Zn–Y–Zr alloys

Abstract

In the present work, the effects of Zn content on the microstructures and mechanical properties of as cast Mg–xZn–5Y–0·6Zr alloys (x?=?2, 5, 8 and 13 wt-%) have been investigated. The results show that the ternary Mg–Zn–Y phase compositions change with Zn/Y ratios induced by the change in Zn content. It is found that the fracture is mainly decided by the characteristics and distribution of second phase rather than the grain size. The influences of these phases, especially the W phase, on the mechanical properties of the alloys have been discussed. Both ultimate tensile strength (UTS) and elongation decrease with the increase in Zn content, while the instance of yield strength (YS) is just the reverse. The W phase is easily cracked because of its brittleness and easy to result in decohesion from the matrix because of the weak atomic bonding, which greatly degrade the UTS and elongation. It can be concluded that the YS closely depends on the grain size, while UTS and elongation closely depend on the volume fraction of eutectic compound (α-Mg+W phase).     

Poisoning of Zr microstructures during casting homogenisation and solution treatment

The influence of Al–Ti–B grain refiners on the microstructures of Zr-containing Al–Zn–Mg–Cu alloy was investigated by optical microscopy and scanning electron microscopy, as well as through tensile and hardness tests. A poisoning effect occurred when the grain refiner was added to the Zr-containing alloy, and the grain size increased significantly. The precipitates in the alloy without the grain refiner were finely distributed, while the phases of the alloy with the Al–Ti–B refiner agglomerated at the grain boundaries, decreasing both the hardness and elongation. The addition of the grain refiner to the alloys markedly increased their hardness and elongation, when coupled with slow cooling, although the peak stress also decreased slightly.     

Effects of Y and Zn/Y on hot tearing susceptibility of Mg–Zn–Y–Zr alloys

The effects of Y and Zn/Y on hot tearing susceptibility (HTS) of Mg–6.5Zn–xY–0.5Zr (x?=?4, 9, 12 and 18) and Mg–5Zn–13.5Y–0.5Zr alloys were investigated herein. The results illustrated that HTS of the investigated alloys decreased in the following order: Mg–6.5Zn–4Y–0.5Zr?>?Mg–6.5Zn–18Y–0.5Zr?>?Mg–6.5Zn–9Y–0.5Zr?>?Mg–6.5Zn–12Y–0.5Zr?>?Mg–5Zn–13.5Y–0.5Zr. The results also showed that HTS of the α-Mg-based alloy containing only LPSO phase was lower than that of the alloy containing only W-phase and (I+W) or (W+LPSO) mixed secondary phases. This was attributed to the coherence relationship between LPSO phase and α-Mg, and the bridging effect of LPSO phase.     

Simultaneously Improved Bendability and Strength of Al–Mg–Si–Cu–Zn Alloys by Controlling the Formation and Evolution of Primary Fe-Rich Phase

In present work, the formation, evolution, and distribution of the primary Fe-rich phase in an Al–Mg–Si–Cu–Zn–Fe–Mn alloy are coupling controlled by ultrasonic melt treatment (USMT) and thermomechanical processing (TMP). It is shown in the results that the size of grains and Fe-rich phase in the as-cast state can be greatly reduced by the applied optimum USMT at 680 °C. Additionally, the transformation rate of β-Fe-rich phase to α-Fe-rich phase can be also enhanced. After the coupling control of USMT and TMP, the number density and distribution uniformity of multiscale Fe-rich particles can be greatly increased or improved, which contributes to the fine-grained recrystallization microstructure and weakened texture. Finally, compared with the 6xxx series Al alloys (such as AA6016 and AA6111), the alloy sheet in the pre-aging state exhibits substantially improved bendability and strength (the plastic strain ratio and tensile strength are 0.67 and 304 MPa, respectively). The effect of USMT on the formation and transformation of primary Fe-rich phase and the mechanisms of improved bendability and strength are deeply discussed.     

Al—Si—Cu—Mg系合金W（AlxSi4Mg5Cu4）相与Al2Cu相的显示与鉴别

研究了Ａｌ－Ｓｉ－Ｃｕ－Ｍｇ系中富铜的Ｗ（ＡｌｘＳｉ４Ｍｇ５Ｃｕ４）相与Ａｌ２Ｃｕ相的金相显示鉴别法，并用化学染色试剂彩色显示区分铸造铝硅铜镁系合金（α＋Ｓｉ＋Ａｌ２Ｃｕ＋Ｗ）四元共晶中的Ｗ相及Ａｌ２Ｃｕ相。     

Strain aging of pearlitic steel wire during post­drawing heat treatments

Abstract

The thermal treatment involved in galvanising affects the mechanical properties of cold drawn pearlitic steels. There is a trough in the ductility at short heating times, which recovers after further heating, but only at the expense of strength. The objective of this work was to gain an understanding of the underlying processes that lead to these changes in properties. A 0.85 wt-%C, vanadium microalloyed, fully pearlitic steel was studied. Samples were heat treated for up to 90 s in a salt bath at 500°C to simulate the galvanising process. The effects of the post­drawing heat treatment on the microstructure and carbon atom distribution were investigated using differential scanning calorimetry, SEM, TEM, and atom probe field ion microscopy. Carbide fragmentation occurs during the heat treatment, representing the onset of the spheroidisation process. The carbon concentration in the ferrite matrix remains low in all heat treatment conditions. However, localised regions of ferrite containing approximately 2.5 at.-%C are observed, indicating the presence of Cottrell atmospheres around dislocation lines. Planar regions enriched in carbon are also seen, which demonstrate segregation to ferrite sub­boundaries. A simple model of the carbon redistribution process is proposed.     

Non-isothermal aging of a high-Zn-containing Al–Zn–Mg–Cu alloy: microstructure and mechanical properties

The non-isothermal aging behaviour of a newly developed Al–Zn–Mg–Cu alloy containing 17?wt-% Zn was investigated. Hardness and shear punch tests demonstrated that during non-isothermal aging, the mechanical properties of the alloy first increased and then decreased. The best properties were obtained in a sample which was non-isothermally aged upto 250°C with heating rate of 20°C?min^?1, due to the presence of η′/η (MgZn₂) phases. This was confirmed by differential scanning calorimetery. After homogenisation, residual eutectic phases remained at triple junctions or in a spherical form. During aging, these phases transformed into rodlike S (Al₂CuMg)-phase at 400°C, with sizes ranging from 50 to 250?nm. The precipitation sequence in this high-Zn alloy was similar to that for conventional Al–Zn–Mg–Cu alloys.     

Hot tensile deformation behaviors and constitutive model of an Al–Zn–Mg–Cu alloy

The hot tensile deformation behaviors of an Al–Zn–Mg–Cu alloy are studied by uniaxial tensile tests under the deformation temperature of 340–460 °C and strain rate of 0.01–0.001 s⁻¹. The effects of deformation temperature and strain rate on the hot tensile deformation behaviors and fracture characteristics are discussed in detail. The Arrhenius-type constitutive model is developed to predict the peak stress under the tested deformation condition. The results show that: (1) The true stress–true strain curves under all the tested deformation conditions are composed of four distinct stages, i.e., elastic stage, uniform deformation stage, diffusion necking stage and localized necking stage. The flow stress decreases with the increase of deformation temperature or the decrease of strain rate. (2) The elongation to fracture increases with the increase of deformation temperature. Under the tested conditions, the strain rate sensitivity coefficient varies between 0.1248 and 0.2059, which indicates that the main deformation mechanism is the lattice diffusion-controlled dislocation climb. (3) The localized necking causes the final fracture of specimens under all the deformation conditions. Microvoids coalescence is the main fracture mechanism under relatively low deformation temperatures. With the increase of deformation temperature, the intergranular fracture occurs. (4) The peak stresses predicted by the developed model well agree with the experimental results, which indicate the validity of the developed model.     

Microstructure and mechanical properties of as-extruded AZ80–xSn magnesium alloys

The effect of 0–2?wt-% Sn addition on AZ80 magnesium alloys after 350°C extrusion has been studied by analysing microstructure and mechanical properties. The results indicated that dynamically recrystallised grains were fine and homogeneous with less than 1?wt-% Sn addition. In AZ80–0.5Sn alloy, a large number of Mg₁₇Al₁₂ precipitated phases formed in grains and at grain boundaries during extrusion process. With more than 1?wt-% Sn addition, the size of dynamically recrystallised grains increased and the number of Mg₁₇Al₁₂ phases decreased. The strength of as-extruded AZ80–0.5Sn alloy enhanced largely as compared with that of the as-extruded AZ80 alloy. AZ80–0.5Sn alloy had the outstanding tensile and compressive properties.     

Eutectic alloys based on the Al–Zn–Mg–Ca system: microstructure,phase composition and hardening

The experimental study of aluminium alloys based on the Al–Ca–Zn–Mg system (3.5% Mg and 2.5% Mg, 0–10% Ca, 0–14% Zn (wt-%)) was combined with Thermo-Calc simulations for the optimisation of the alloy composition. Zinc is distributed between aluminium solid solution and phase (Al,Zn)₄Ca. Magnesium was not observed in the intermetallic phase. The eutectic (Al,Zn)₄Ca had fine structure and particles of (Al,Zn)₄Ca were capable of spheroidisation during the heat treatment at 520°С. The maximum level of hardness observed in calcium-containing alloys was higher than 200 HB, suggesting good strength properties. With an example of the Al–Zn(9%)–Mg(3.5%)–Ca(3%) alloy, the possibility of manufacturing thin rolled sheets based on the (Al)–Ca eutectic was demonstrated.

This article is part of a Themed Issue on Aluminium-based materials: processing, microstructure, properties, and recycling.     

Microstructure and mechanical properties of a new Al–Zn–Mg–Cu alloy joints welded by laser beam

A new type of Al–Zn–Mg–Cu alloy sheets with T6 temper were welded by laser beam welding (LBW). Microstructure characteristics and mechanical properties of the joints were evaluated. Results show that grains in the heat affected zone (HAZ) exhibit an elongated shape which is almost same as the base metal (BM). A non-dendritic equiaxed grain zone (EQZ) appears along the fusion line in the fusion zone (FZ), and grains here do not appear to nucleate epitaxially from the HAZ substrate. The FZ is mainly made up of dendritic equiaxed grains whose boundaries are decorated with continuous particles, identified as the T (AlZnMgCu) phase. Obvious softening occurs in FZ and HAZ, which mainly due to the changes of nanometric precipitates. The precipitates in BM are mainly η′, while plenty of GPI zones exist in FZ and HAZ adjacent to FZ, in the HAZ farther away from FZ, η phase appears. The minimum microhardness of the joint is always obtained in FZ at different times after welding. The ultimate tensile strength of the joint is 471.1 MPa which is 69.7% of that of the BM. Samples of the tensile tests always fracture at the FZ.     

Heating aging behavior of Al–8.35Zn–2.5Mg–2.25Cu alloy

In the present work, the influence of heating aging treatment (HAT) on the microstructure and mechanical properties of Al–Zn–Mg–Cu alloy was investigated. When the final aging temperature (FAT) was lower than 180 °C, the hardness increased with the decreasing of heating rate, however, in the case of the FAT was higher than 180 °C, the variation of hardness was opposite. The electrical conductivity of Al–Zn–Mg–Cu alloy increased with the decrease of heating rate regardless of FAT. The tensile strength, yield strength and conductivity of the Al alloy after (100–180 °C, 20 °C/h) HAT increased by 1.6%, 4.5% and 14.1% than that after T6 treatment, respectively. The precipitates sequence of HAT was coincident with that of isothermal aging, which is SSS → GP zone → η′ → η. With the increase of FAT and the decrease of heating rate, the fine precipitates became larger and the continuous η phase at grain boundary grew to be individual large precipitates. The HAT time was decreased about 80% than that for T6 treatment, indicating HAT could improve the mechanical properties, corrosion resistance and production efficiency with less energy consumption.     

On fatigue lives of diecast and extruded Mg alloys

In this study, fatigue tests were carried out on both diecast and extruded Mg alloys to study their distributions of fatigue lives under constant stress amplitudes. During the fatigue process of the diecast Mg alloy, cracks initiated from the casting defects inside of the specimen, and then propagated prior to final failure of the specimen. While in the extruded Mg alloy, cracks initiated from the inclusions located on the specimen surface. With assuming the above defects as the initial cracks, the initial maximum stress intensity factors K_imax were evaluated. There are common relations between the initial maximum stress intensity factors K_imax and fatigue lives N_f, regardless of the stress amplitudes for the both Mg alloys at the constant R ratio of −1. The lower K_imax, the longer N_f becomes. Integrating the fatigue crack propagation law from the initial maximum stress intensity factor K_imax to the fatigue fracture toughness K_fc, the relations K_imax vs. N_f can be successfully evaluated.Distributions of fatigue lives at the constant stress amplitudes can be represented by the Weibull distributions. Dispersion in the fatigue lives becomes larger at the lower stress amplitude as compared with those at the higher stress amplitudes. This trend is observed commonly for both diecast and extruded Mg alloys.     

Microstructure,phase evolution and corrosion behaviour of the Zn–Al–Mg–Sb alloy coating on steel

ABSTRACT

In the present work, the influence of antimony (Sb) addition in Zn–Al–Mg alloy on the microstructure, phase characteristic, solidification behaviour and corrosion resistance of hot dipped Zn–0.5Al–0.5Mg–xSb (x?=?0, 0.1, 0.3 and 0.5?wt-%) coated steel wires were evaluated. Thermal analysis revealed that cooling rate of the liquid metal using the steel mould (5.3°C?s^–1) was higher than using ceramic mould (0.3°C?s^–1). Based on the phase analysis and verified by thermodynamic calculations, it was revealed that Zn₁₁Mg₂ and Zn₂Mg phases appeared for Zn–Al–Mg alloy at slow and fast cooling rates while, the Mg₃Sb₂ phase was observed after addition of Sb at both cooling rates. Corrosion behaviour of the alloys determined through electrochemical measurements shows that Zn–Al–Mg alloy with 0.3?wt-%Sb has the lowest corrosion rate indicating an excellent corrosion resistance.     

Microstructure and mechanical property of high strength Mg–Sn–Zn–Al alloys

This paper aims to reveal the microstructure and mechanical properties of as-cast and hot-rolled Mg–Sn–Zn–Al based alloys. Three alloys, Mg–5Sn–2Zn (TZ52), Mg–5Sn–2Zn–2Al (TAZ522) and Mg–5Sn–5Al–1Zn–0.2Mn (TAZM5510) alloys were studied. The results revealed that the as-cast alloys showed fine dendritic structures. The TAZM5510 alloys exhibited moderate yield strength of 98?MPa with good elongation of ～15%, which was comparable to several commercially used Mg die-castings. Mechanical properties were significantly improved after multi-pass rolling. The TZ52 sheet showed a high yield strength of 277?MPa with excellent ductility exceeding 30%, and the TAZM5510 sheet exhibited the highest tensile strength of 386?MPa while keeping desirable elongation of 16.6%. These sheets are termed as strong and ductile Mg–Sn–Zn–Al wrought alloys.     

Effect of Homogenization Process on Microstructure of Al–Zn–Mg–Cu Aluminum Alloys

Herein, the best homogenization process of 466.5 °C × 36 h + 490 °C × (14–26.4 h) that can completely eliminate the coarse phases σ[Mg(Zn, Al, Cu)₂] and S(Al₂CuMg) in the Al–Zn–Mg–Cu aluminum alloy is developed. The homogenization process is determined by the method of calculation phase diagram, and the experimental verification. It is shown in the results that, first, in the microstructure of the as-cast alloys, the crystal structure of the σ[Mg(Zn, Al, Cu)₂], Al₇Cu₂Fe, and Mg₂Si phases is determined. Second, during the homogenization process, the σ[Mg(Zn, Al, Cu)₂] phase dissolves and also transforms into the S(Al₂CuMg) phase. Most importantly, the dissolution temperature range of the σ[Mg(Zn, Al, Cu)₂], S(Al₂CuMg), and Al₇Cu₂Fe phases is determined from 472.56 to 476.36 °C, from 484.09 to 485.39 °C, and from 540.18 to 547.23 °C, respectively. At best homogenization process, the residual Al₇Cu₂Fe phase area fraction ranges from 1.28 ± 0.16% to 1.60 ± 0.18%. In addition, dispersed η(MgZn₂) phase precipitates in supersaturated Al-matrix during differential scanning calorimeter heating. And, the concentration differences between the grain center and the eutectic of structure of Zn, Mg and Cu regression equations are established, which can provide some reference for the design of experimental parameters, thus reducing the experimental workload.