深过冷Sb-Sn过包晶合金的快速凝固

采用落管无容器处理技术研究了Sb74.7Sn25.3二元过包晶合金的快速凝固,获得的合金粒子直径D介于70～1080μm之间。理论计算表明,随着粒子直径的减小,过冷度和冷却速率均呈指数关系增大,最大过冷度为298K(0.36TL)。研究发现,在自由落体条件下,快速凝固组织由初生Sb固溶体相和包晶SbSn金属间化合物相组成,Sb固溶体相以非小平面和小平面两种生长方式长大。当过冷度增大时,释放的熔化潜热增多,初生相逐渐细化,非小平面初生Sb相由"粗大枝晶"向"碎断枝晶"转变,当D<400μm时,一次枝晶臂显著变短,二次枝晶间距明显减小;同时发生溶质截留现象,初生Sb固溶体相中溶质Sn的固溶度发生了显著拓展,由ΔT=32K时的7.86%(原子分数,下同)线性增大至ΔT=298K时的10.47%。     

稀土Er对A356铝合金微观组织和力学性能的影响

针对传统的A356铝合金,添加稀土元素是改善其微观组织并提高力学性能的有效途径。本工作通过示差扫描量热分析(DSC)、X射线衍射(XRD)、扫描电镜(SEM)等分析手段来研究稀土Er对铸态A356铝合金组织和性能的影响。结果表明,稀土元素Er是一种能够显著改善A356合金铸态组织的优良变质剂。Er的加入细化了初生α-Al相,二次枝晶间距降低,枝晶臂直径减小,同时对铸态组织中的共晶Si起到了变质作用。当Er含量达到0.4%(质量分数,下同)时,细化效果最为显著,二次枝晶间距由53.6μm减小到17.5μm,共晶硅形貌也由粗大的板条状转变为短棒或圆粒状。与A356合金相比,添加0.4%Er的合金样品的抗拉强度和伸长率分别提高了15.1%,29.8%。     

快速凝固AlCoCrFeNi2.1共晶高熵合金的微观组织演变和力学性能

使用真空快速凝固设备制备不同直径的AlCoCrFeNi_2.1合金铸棒和薄带,研究了冷却速率对多主元共晶高熵合金的微观组织和力学性能的影响。结果表明,全部试样均由FCC和B2两相组成。不同直径的合金铸棒均为常规共晶组织,只在表层某些位置观察到胞状共晶组织。铸棒的直径越小,冷却速率越大,规则共晶组织的片间距(λ)越小,其屈服强度越高。当铸棒直径由8 mm减小至2 mm时表层区域的λ值由530.4 μm减小至357.0 μm,轴心区域的片间距由712 μm减小至474 μm,合金的屈服强度由690 MPa提高到877 MPa。结合合金薄带的微观组织分析结果表明,随着冷却速率的提高AlCoCrFeNi_2.1合金依次形成规则和非规则混合共晶组织、胞状共晶组织和树枝状组织。     

熔渗温度对Si/Al复合材料组织及性能的影响

采用无压熔渗法制备Si/Al复合材料,研究了熔渗温度对所制备Si/Al复合材料Si相形貌的影响,对Si相间基体合金的凝固组织进行了分析,测试了Si/Al复合材料热膨胀系数、热导率及抗弯强度。结果表明,在相同熔渗时间下,随着熔渗温度升高,所制备Si/Al复合材料中Si相从颗粒状到形成网络状。Si相间的Al-Si基体合金中不再是典型的初生相和共晶组织,而是出现了类似离异共晶的结晶现象,即初晶Si和共晶Si是在原存的Si相上结晶长大。XRD分析显示在所制备复合材料中只有Si相和Al相。随着熔渗温度升高复合材料热膨胀系数、热导率以及抗弯强度均出现下降。     

Interface morphology evolvement and microstructure characteristics of hypoeutectic Cu–1.0 wt%Cr alloy during unidirectional solidification

Effect of unidirectional solidification rate on microstructure of hypoeutectic Cu–1.0%Cr alloy was investigated. The microstructure evolution of Cu–1.0%Cr alloy was noticed especially during the unidirectional solidification with the different solidification rates. It is shown that eutectic (α+β) and primary α(Cu) phase grew up equably in parallel to direction of solidification. A kind of fibriform microstructure will appear when unidirectional solidification rate is up to some enough high certain values. When temperature gradient was changeless, the interface morphology evolution of the primary α(Cu) phase underwent to a series of changes from plane to cell, coarse dendrite, and fine dendrite grains with increasing the solidification rates. Primary dendrite arm spacing λ1 of α(Cu) phase increases with increasing the solidification rate where the morphology of the solid/liquid (S/L) interface is cellular. However, λ1 decreases with further increasing the solidification rate where the S/L interface morphology is changed from cell to dendrite-type. Its rule might accord with Jackson–Hunt theory model. An experience equation obtained is as follows: . On the other hand, secondary dendrite spacing λ2 of primary α(Cu) phase will thin gradually with increasing the solidification rate. Moreover, secondary dendrite will become coarse in further solidification. Another experience equation about relationship among secondary dendrite arm spacing (λ₂), temperature gradient G_L and the velocity of the S/L interface (V) is that: λ₂=−0.0003+0.0027(G_LV)^−1/3. In addition, the volume fraction of eutectic will decrease with the increase of solidification rate.     

Evaluation of primary dendrite trunk diameters in directionally solidified Al-Si alloys

Hypoeutectic Al-Si alloys were directionally solidified under conditions of steady-state growth. Cross-sectional views of the microstructure, i.e., perpendicular to the growth direction, were examined and measurements of the primary dendrite trunk diameters made. The results are presented as functions of growth velocity, composition, and temperature gradient, and evaluated in terms of relevant theory. It is suggested that the primary dendrite trunk diameter is a reliable, or better, a measure of the local solidification conditions during constrained growth than either the conventionally accepted eutectic (λ_E) or primary dendrite arm (λ₁) spacing.     

Microstructure and solidification behavior of Cu–Ni–Si alloys

The microstructure and solidification behavior of Cu–Ni–Si alloys with four different Cu contents was studied systematically under near-equilibrium solidification conditions. The microstructures of these Cu–Ni–Si alloys were characterized by SEM and the phase composition was identified by XRD analysis. The phase transition during the solidification process was studied by DTA under an Ar atmosphere. The results show that the microstructure and solidification behavior is closely related to the composition of Cu–Ni–Si alloys. The microstructure of Cu–Ni–Si alloys with higher than 40% Cu content consists of primary phase α-Cu(Ni, Si) and eutectic phase (β₁-Ni₃Si + α-Cu(Ni,Si).When the Cu content is about 40%, only the eutectic phase (β₁-Ni₃Si + α-Cu(Ni,Si)) is present. DTA analysis shows there are three phase transitions during every cooling cycle of alloys with higher than 40% Cu content, but only one for 40% Cu content. Cu–Ni–Si alloy with 40% Cu solidifies by a eutectic reaction, but Cu–Ni–Si alloys with higher than 40% Cu content solidify as a hypoeutectic reaction.     

Severe plastic deformation of an as-cast hypoeutectic Al–Si alloy

Different equal channel angular pressing (ECAP) processing routes have been employed to investigate the flow plane microstructures in a hypoeutectic Al–7wt%Si. In the as-cast condition, this alloy exhibits equiaxed primary aluminum dendrite cells embedded in an Al–Si eutectic constituent. The observed microstructures have been compared to the predicted distortion of a volume element expected during idealized ECAP. The effect of different processing routes on the microstructure refinement, degree of homogenization of second phase particles, and associated mechanical properties are discussed.     

Microstructure and properties of a bismuth-indium-tin eutectic alloy

A ternary eutectic alloy with a composition of 57.2%Bi, 24.8%In and 18%Sn was continuously cast into wire of 2 mm diameter with casting speeds of 14 and 79 mm min^–1 using the Ohno continuous casting process. The microstructures and mechanical properties of the wires were compared with those of statically cast specimens. Extensive segregation of massive bismuth crystals, bismuth complex structures, and tin rich dendrites was found in specimens which were statically cast. The bismuth complex-regular structures, which are a ternary eutectic constituent, existed along the boundaries of the BiIn dendrite cells forming a double binary eutectic. In the continuously cast wires, primary tin dendrites coupled with a fine bismuth phase were uniformly distributed within the Bi-In alloy matrix. With this novel, net-shape, casting process, the formation of massive bismuth crystals, bismuth complex-regular structures and BiIn eutectic dendrite cells was prevented, resulting in a more uniform microstructure which was in contrast to the heavily segregated structures of the statically cast specimens. These differences in structure significantly affected the mechanical properties. The continuously cast wires exhibited considerable ductility in contrast with the statically cast specimens which had lower toughness and exhibited cleavage fracture with little or no elongation at higher strain rates.     

Strain path and microstructure evolution during severe deformation processing of an as-cast hypoeutectic Al–Si alloy

Microstructure evolution in an as-cast Na modified Al–7%Si (wt. pct.) alloy was examined during redundant and monotonic straining by repetitive equi-channel angular pressing (ECAP) under ambient temperature conditions, and during friction stir processing (FSP). Redundant straining during repetitive ECAP was accomplished by processing following route B_C while monotonic straining employed route A. Single- and multi-pass FSP was conducted on this same as-cast material using an FSP tool having a threaded pin. The as-cast microstructure comprises equiaxed primary α dendrite cells embedded in the Al–Si eutectic constituent. The evolution of this microstructure during repetitive ECAP can be described by idealized models of this process. The primary and eutectic constituents can still be discerned and the Si particle distribution is not homogenized even during ambient temperature processing involving von Mises strains >9.0. In contrast, the primary and eutectic constituents cannot be distinguished in the stir zone after even a single FSP pass. Strain estimates based on the shape change of the primary α constituent indicate that the Si particle distribution has become homogeneous at local von Mises strains of 2.5–3.0 during the FSP thermomechanical cycle. Mechanical property data are consistent with strain path during SPD processing by repetitive ECAP and FSP.     

稀土元素Gd对Al-Si-Mg铸造合金微观组织和力学性能的影响

为了系统地研究稀土Gd对铸造Al-Si-Mg(A357)合金组织和性能的影响,采用OM,SEM,EPMA,XRD,DSC,TEM及拉伸实验等方法对不同Gd含量A357合金进行研究。结果表明:Gd的添加可以细化A357合金的晶粒并减小二次枝晶间距。此外,Gd可以有效地细化合金中的共晶硅,但是对片状共晶硅的形貌影响不大。晶粒和共晶硅的细化及二次枝晶间距的减小使添加Gd后的A357合金的力学性能有了显著的提高。其中,A357-0.5Gd(质量分数/%)合金热处理态抗拉强度为355MPa,相对于未添加Gd元素的A357合金提高了37MPa。当Gd质量分数为1.0%时,尽管组织得到进一步细化,但是大量粗大Al 2Si 2Gd第二相的形成导致了合金力学性能的下降。同时对Gd的细化机制进行探究,结合TEM分析结果可以推断,Gd变质处理后共晶硅上的孪晶密度并不足以引起共晶硅形貌的转变,使得Gd变质效果较弱。而Gd对共晶硅的细化作用可能与Gd增加成分过冷以及形成纳米相阻碍共晶硅生长有关。     

自生TiC增强钛基复合材料的微观组织

采用反应自生法制备了ＴｉＣ颗粒增强钛合金基复合材料,研究了复合材料的相组成和微观组织。在Ｔｉ－６Ａｌ－２Ｃ合金中存在Ｔｉ和ＴｉＣ两种相。ＴｉＣ权树枝状初生Ｔｉｃ和短棒状共晶ＴｉＣ两种开头存在,其中共晶ＴｉＣ主要存在于晶界,特别是三角晶界处。ＴｉＣ晶格常数的计算结果表明ＴｉＣ的衍射峰存在一定的偏移,主要是由于存在于ＴｉＣ中的Ｃ空位引起晶格畸变。随着Ａｌ含量的增加,初生ＴｉＣ由发达粗大的树枝晶变为不发达的树枝晶,当Ａｌ含量为３５％时变为短棒状和薄片状的ＴｉＣ。基体组织也相应地由单一的Ｔｉ基体变为Ｔｉ和Ｔｉ３Ａｌ的两相基体以及Ｔｉ３Ａｌ和ＴｉＡｌ两相基体。根据相图分析了组织变化的主要原因。     

The influence of Sr,Mg and Cu addition on the microstructural properties of a secondary AlSi9Cu3(Fe) die casting alloy

The influence of Sr, Mg and Cu content on the microstructure of a high-pressure die cast AlSi9Cu3(Fe) alloy is reported. Metallographic and image analysis techniques have been used to quantitatively examine the microstructural changes occurring at different Sr, Mg and Cu levels. The results reveal that the Sr and Cu increase the amount of microporosity in the die castings, while Mg counteracts this effect. The secondary dendrite arm spacing and the grain size slightly decrease by the addition of the alloying elements. Compared with the base AlSi9Cu3(Fe) alloy, the Sr-modified alloy shows significant refinement and morphological modification of eutectic Si particles in the central regions of the castings. In contrast, such mechanisms at the casting surfaces are substantially driven by more rapid solidification. The Mg and Cu addition annihilates the benefits of refinement of eutectic Si particles by Sr modification, while it seems to not affect their morphology. The combined addition of Cu and Mg determines an increase of Cu- and Mg-rich intermetallic compounds, while the Sr-modified alloy shows lower fraction of intermetallics, even if comparable to the base alloy in terms of other alloying elements.     

Phase growth patterns for Al_2O_3/GdAlO_3 eutectics over wide ranges of compositions and solidification rates

Phase selection and growth characteristics of directionally solidified Al₂O₃/GdAlO_3(GAP)faceted eutectic ce ramics are investigated over wide ranges of compositions and solidification rates to explore the eutectic coupled zone.Through the obse rvation of the quenched solid-liquid interface,the competitive growth of primary faceted Al₂O₃phase,prima ry non-faceted GAP phase and Al₂O₃/GAP eutectic with diffe rent morphologies is detected.Microstructure transitions from wholly eutectic to primary Al₂O₃(GAP)dendrite plus eutectic and then to wholly eutectic are found in Al₂O₃-2 O mol%Gd₂O₃hypoeutectic(Al₂O₃-26 mol%Gd₂O₃hypereutectic)ceramics with the increase of solidification rate.The dendrite growth of faceted Al₂O₃and non-faceted GAP phases are well predicted by KGT model,which have introduced appro p riate dimensionless supersaturationΩto characterize the anisotropic growth of dendrites.Based on the maximum interface temperature criterion,the competitive growth of primary phase and eutectic is analyzed theoretically and the predicted coupled zone of Al₂O₃/GAP eutectic ceramics is in good agreement with the experimental results.Besides,the influence of microstructure with these different morphologies on the flexural strength of Al₂O₃/GAP eutectic ceramics is studied.     

Low temperature diffusion of Au into Si in the Si(substrate)-Au(film) system

When the clean surface of a Si crystal is covered with an evaporated Au layer and heated in an oxidizing atmosphere at 100°–300°C, i.e. below the Si-Au eutectic point (370°C), Si atoms are ejected from the Si-Au interface and migrate through the Au film to its surface to appear as a SiO₂ layer. For an understanding of this low temperature ejection, an AES study of the Si-Au interface region has been undertaken. It is proposed that the Si at the interface is metallic and forms a metallic bonding with Au, the melting point of the interface being comparable with that of Si-Au eutectic. The metallic Si was identified from Si (LVV) Auger spectra of “vapor-quenched” metastable Si-Ag, Si-Au and Si-Cu alloys. The low temperature ejection is possible, therefore, from this metallic interface. To support this statement, low temperature ejection of Au atoms from the interface into the bulk of Si was also studied by photoconductivity measurements of the above specimen. The analysis of the photoresponse spectra of the ejected Au atoms inside the Si crystal suggests that the atoms diffuse interstitially with a diffusion coefficient of about 10^-9 cm² sec^-1 at 340°C.     

深过冷Fe-B-Si共晶合金凝固组织纳米化机制探讨

采用深过冷及深过冷加水淬的方法,成功地制备了样品直径为16mm,高为15mm,组织中晶粒平均尺寸小于120nm的Fe76B12Si12合金块体纳米材料。理论分析与实际计算结果表明：该合金凝固组织纳米化的主要原因在于,其共晶两相的生长速度小、组织粗化速率小、溶质平衡分配系数低以及具有相对较低的熔化焓;深过冷Fe-B-Si合金块体纳米软磁材料制备的理想条件是：获得超过冷、选择主要由溶质扩散控制生长的共晶合金成分、获得Fe2B(Si)相为完全准球状形态的二次粒化非规则共晶组织。     

Eutectic spacing and faults of directionally solidified Al–Al3Ni eutectic

The Al–Al₃Ni eutectic was directionally solidified at a thermal gradient of 4.5 K/mm in a vacuum Bridgman–type furnace in order to study eutectic spacing selection criterion.The microstructure was examined in transverse and longitudinal sections and the interrod spacings were measured at different growth velocity. It has been shown that the interrod spacing is not unique and displays a limited range for rodlike Al–Al₃Ni eutectic alloy. The initial growth velocities are not responsible for the eutectic spacing range, while such faults as branching, endingand diameter change have a significant influence on the eutectic spacing adjustment.     

Effects of high magnetic fields on solidification microstructure of Al–Si alloys

The effects of high magnetic fields on the solidification microstructure of Al–Si alloys were investigated. Al–7.2 wt%Si and Al–11.8 wt%Si alloys were solidified in various high magnetic fields at different cooling rates. The secondary dendrite arm spacing (SDAS) of the primary Al dendrites and the lamellar spacing (LS) of the eutectics were measured. It was found that the application of a high magnetic field could decrease the SDAS of the primary Al dendrites in Al–7.2 wt%Si alloys and the LS of the eutectics in Al–11.8 wt%Si alloys. The effects of the high magnetic field on the SDAS decreased with increasing cooling rate. The decrease in the SDAS and LS can be attributed to the decrease of the solute diffusivity in the liquid ahead of the solid/liquid interface during the growth of the dendrite and eutectic. This decrease is caused by the high magnetic field which can damp the convection and avoid its contributions to the diffusion.     

Eutectic spacing and faults of directionally solidified Al–Al3Ni eutectic

The Al–Al₃Ni eutectic was directionally solidified at a thermal gradient of 4.5 K/mm in a vacuum Bridgman-type furnace in order to study eutectic spacing selection criterion. The microstructure was examined in transverse and longitudinal sections and the interrod spacings were measured at different growth velocity. It has been shown that the interrod spacing is not unique and displays a limited range for rodlike Al–Al₃Ni eutectic alloy. The initial growth velocities are not responsible for the eutectic spacing range, while such faults as branching, ending and diameter change have a significant influence on the eutectic spacing adjustment.     

Study of grain refinement and eutectic transformation of undercooled IN718 superalloy

Abstract

A substantial undercooling up to 250 K was produced in the IN718 superalloy melt by employing the method of molten salt denucleating, and the microstructure evolution with undercooling was investigated. Within the achieved undercooling, 0–250 K, the solidification microstructure of IN718 undergoes two grain refinements: the first grain refinement occurs in a lower range of undercooling, which results from the ripening and remelting of the primary dendrite, and at a larger range of undercooling, grain refinement attributes to solidification shrinkage stress and lattice distortion energy originating from the rapid solidification process. A ‘lamellar eutectic anomalous eutectic’ transition was observed when undercooling exceeds a critical value of ～250 K. When undercooling is small, owing to niobium enrichment in interdendrite, the remaining liquid solidifies as eutectic (γ+Laves phase); whereas, if the undercooling achieves 250 K, the interdendrite transforms from eutectic (γ+Laves phase) to Laves phase, which results from the formation of divorced eutectic arising from the huge variance of the growth velocities of γ and Laves phases.