Experimental determination of thermal conductivity of solid and liquid phases in Bi−Sn and Zn−Mg binary eutectic alloys

The thermal conductivities of solid phases, K_s, for Bi-43 wt.% Sn and Zn-0.15 wt.%Mg binary alloys at their eutectic temperature are found to be 28.0 τ 1.4 and 137.4–6.9 W/Km, respectively, with a radial heat flow apparatus. The thermal conductivity ratios, R, of liquid phase to solid phase for the same alloys at their eutectic temperature are found to be 0.93 and 0.78, respectively, with a Bridgman type directional solidification apparatus. Thus, the thermal conductivities of the liquid phases, K_L, for Bi-43 wt.%Sn and Zn-0.15 wt.%Mg binary alloys at their eutectic temperature are evaluated to be 26.0−1.3 and 107.2−5.4 W/Km, respectively, from the measured values of K_s and R.     

Effect of growth rates and temperature gradients on the spacing and undercooling in the broken-lamellar eutectic growth (Sn-Zn eutectic system)

The Sn-Zn system has a eutectic structure of a broken lamellar type. Dependence of the broken-lamellar spacing λ and the undercooling ΔT on V and G were investigated, and the relationship between them was examined. A Sn-Zn (99.99%) high-purity eutectic alloy was melted in a graphite crucible under vacuum atmosphere. This eutectic alloy was directionally solidified upward with a constant growth rate V (8.30 μm/s) and different temperature gradients G (1.86–6.52 K/mm), and also with a constant temperature gradient (6.52 K/mm) and different growth rates (8.30–165.13 μm/s) in a Bridgman-type directional solidification furnace. The lamellar spacings λ were measured from both transverse and longitudinal sections of the specimen. The λ values from the transverse section were used for calculations and comparisons with the previous works. The undercooling values ΔT were obtained using growth rate and system parameters K ₁ and K ₂. It was found that the values of λ decreased while V and G increased. The relationships between lamellar spacing λ and solidification parameters V and G were obtained by linear regression analysis method. The λ² V, ΔTλ, ΔTV ⁻⁵, and λ³ G values were determined using λ, ΔT, V, and G values. The experimentally obtained values for the broken-lamellar growth (Sn-Zn eutectic system) were in good agreement with the theoretical and other experimental values.     

Experimental determination of interfacial toughness curves

The evaluation of mixed-mode interfacial fracture toughness is of great importance for the integrity of electronic devices because interfacial cracks are subjected to mixed-mode loading by vapor pressure, thermal stress and other factors. A lot of work has been done to clarify the unusual characteristics of the fracture of bimaterial interfaces. Since interfacial fracture toughness (G _c) greatly depends on phase angle (Ψ), most work has focused on the determination ofG _c-Ψ curves using various specimens. However, this requires a lot of time, expense and effort. In this work, theG _c-Ψ curves of oxidized Cu-based leadframe/EMC (epoxy molding compound) interfaces were determined by measuring interfacial fracture toughness under mode-I, mode-II and mixed-mode loading conditions using sandwiched-double-cantilever-beam (SDCB) specimens, Arcan specimens and sandwiched-Brazilian-nut (SBN) specimens, respectively. The experimental results showed that the measuredG _c-Ψ curves obeyed theG _c-Ψ expression proposed by Ahmad first developed by Evans and Hutchinson based on the micromechanics modeling of mixed-mode fracture. Comparing data in the literature, theG _c-Ψ expression proposed by Ahmad was confirmed to be valid, and a method of predictingG _c-Ψ curves without much experiment was proposed.     

Determination of interfacial energies for solid al solution in equilibrium with Al-Cu-Ag liquid

The equilibrated grain boundary groove shapes of a solid Al solution in equilibrium with Al-Cu-Ag liquid were observed from a quenched sample using a radial heat flow apparatus. The Gibbs-Thomson coefficient, solid-liquid interfacial energy, and grain boundary energy of the solid Al solution were determined from the observed grain boundary groove shapes. The thermal conductivity of the solid phase for Al-16.42 at.% Ag-4.97 at.% Cu and Al-16.57 at.% Ag-11.87 at.% Cu alloys and the thermal conductivity ratio of the liquid phase to the solid phase for Al-16.57 at.% Ag-11.87 at.% Cu alloy at the melting temperature were also measured with a radial heat flow apparatus and a Bridgman-type growth apparatus, respectively.     

Zn固溶量对Mg-Zn-Y合金组织的影响

利用电化学相分离法,成功提取Mg-Zn-Y合金中的第二相,并获得合金元素在Mg-Zn-Y合金中的固溶量,建立了镁合金中直接测定元素固溶量的方法。利用Miedema混合焓模型及Toop模型(对称)和Kohler模型(非对称)计算Mg-Zn-Y三元合金中Zn的活度及活度相互作用系数,通过实验测定及计算表明：Mg-Zn-Y中Zn的自相互作用系数与Y的相互作用系数均为正值,说明这一体系里Zn与Zn,Zn与Y是相互排斥的,Y的存在可以提高Zn的活度,即Y固溶量的增加会导致Zn固溶量的降低,增加了固液界面前沿液相中的成分过冷度,从而使得晶粒细化,晶界处片层状的Mg₃Y₂Zn₃共晶相聚集增多,逐渐连续成网状。     

Room-temperature solid solution softening in Fe-V binary system

Molecular dynamics simulations of the glide of an edge dislocation in the bcc matrix of Fe-V alloys were performed to investigate the room-temperature solid solution softening by V atoms. For this purpose, the glide velocity of an edge dislocation was calculated as a function of V concentration under the shear stresses of 100-300MPa using the Fe-V cross-potential constructed newly in the present study. Whereas the solid solution hardening occurred as the V concentration is less than 0.13 at% or more than 0.5 at%, the room-temperature solid solution softening was observed in Fe-(0.13-0.5) at% V alloys. The solid solution softening occurring in Fe-(0.13-0.5) at% V alloys was caused by the accelerated growth velocity of kinks by solute V atoms. The increase in kink velocity happened when the interatomic distance between solute V atoms was similar to the length of dislocation kinks.     

Phase equilibria of the Au–Sn–Zn ternary system and interfacial reactions in Sn–Zn/Au couples

Phase equilibria of the Au–Sn–Zn ternary system and interfacial reactions between Sn–Zn alloys and Au were experimentally investigated at 160 °C. Experimental results reveal that no equilibrium-stated ternary phases were found and the ternary element solubility in the binary phase is insignificant. When the Zn content was less than 3 wt% in the Sn–Zn alloy, only the Au–Sn binary intermetallic compounds (IMCs), such as AuSn, AuSn₂ and AuSn₄ phases, were formed at the Sn–Zn/Au interface. When the Zn content in Sn–Zn alloys was greater than 7 wt%, the AuZn, AuZn₂ and Au₃Zn₇ phases were formed in the Sn–Zn/Au couples at 160 °C. However, both Sn–Zn and Au–Zn IMCs, and the Au–Zn–Sn ternary IMC (T phase) were observed between Au and the Sn–Zn alloys with 3–5 wt% added Zn. This T phase might be the metastable phase. The evolution of IMCs in the Sn–Zn/Au couples is very sensitive to the Zn content in Sn–Zn alloys.     

Calculation of solid-liquid interfacial free energy and its anisotropy in undercooled system

The solid-liquid interfacial free energy and its anisotropy are crucial quantities in determining the micros tructure and mechanical properties of materials.However, most researches mainly concerned the solidliquid coexistence at melting point. In this work, two methods, the critical nucleus method(CNM) and the capillary fluctuation method(CFM), were combined to get these quantities in undercooled system by molecular dynamics(MD) simulations. The melting point, Tolman length, interfacial free energy and its anisotropy were calculated, and good consistent results from these two methods are obtained. The results of interfacial free energy obtained by CNM and CFM are 103.79 and102.13 mJ·m~(-2), respectively, with the error 2%. Meanwhile, both of the methods provide the rank of interfacial free energy by γ_(100) γ_(120) γ_(110) γ_(112) γ_(111). The results of the present study are also in good agreement with experimental data and computational data in the literature.     

Experimental and theoretical research on interfacial reaction of solid Co with liquid Al

Interfacial reaction between solid Co and liquid Al was investigated with immersion tests and theoretical modeling. The microstructure characterization indicated that a Co₂Al₅ intermetallic layer was formed at solid–liquid interface during the immersion test. The modeling results indicated that the corrosion rate of a solid metal in a liquid metal was controlled by both the formation and dissolution of the intermetallic layer. In Co–Al reaction system, the formation and dissolution of the Co₂Al₅ layer reached an equilibrium state in a very short time, and the corrosion of the Co matrix was mainly dominated by the dissolution of the Co₂Al₅ layer.     

Experimental determination of phase equilibria in the Fe---Al---C system

The phase equilibria in the Fe---Al---C system have been determined between 800 °C and the liquidus surface. From cast alloys the liquidus surface was established. From electron microprobe analyses (EPMA) of quenched samples three isothermal sections at 800, 1000 and 1200 °C have been obtained. Additional high temperature X-ray diffraction experiments (HT-XRD) yielded three vertical sections and the temperatures of four invariant reactions. The influence of carbon on the transition temperature between the disordered (A2) and the ordered (B2) -solid solution was determined from HT-XRD experiments with single crystals. This transition is shifted remarkably to higher temperatures by the addition of carbon. Special emphasis was placed on establishing the homogeneity range of the K-phase and its dependence on temperature. This dependence is discussed in terms of order/disorder. In addition, the properties of the K-phase, lattice constant as function of chemical composition, microhardness and thermal expansion coefficient , have been determined.     

On the interfacial energy of coherent interfaces

A thermodynamic model has been developed for interfacial energies of coherent interfaces using only the molar Gibbs energy and the molar volume of the two phases surrounding the interface as the initial data. The analysis is started from the simplest case of the interface formed by two solutions on the two sides of a miscibility gap, when both phases are described by the same Gibbs energy and molar volume functions. This method is applied to the fcc Au–Ni, liquid Ga–Pb and liquid Al–Bi systems. Reasonable agreement was found with the measured values in liquid Ga–Pb and Al–Bi systems. It was shown that the calculated results are sensitive to the choice of the Calphad-estimated thermodynamic data. The method is extended to the case where the two phases are described by different Gibbs energy and molar volume functions. The extended model is applied to the interface present in an Ni-based superalloy between the AlNi₃ face-centered cubic (fcc) compound and the Ni–Al fcc disordered solid solution. The calculated results are found to be similar to other values recently obtained from the combination of kinetic and thermodynamic data. The method is extended to ternary and higher order systems. It is predicted that the interfacial energy will gradually decrease with the increase in number of components in the system.     

Experimental determination of the phase equilibria in the Co-Fe-Zr ternary system

The phase equilibria in the Co-Fe-Zr ternary system were investigated by means of optical microscopy (OM), electron probe microanalysis (EPMA), X-ray diffraction (XRD), and differential scanning calorimetry (DSC) on equilibrated ternary alloys. Four isothermal sections of the Co-Fe-Zr ternary system at 1300 °C, 1200 °C, 1100 °C and 1000 °C were experimentally established. The experimental results indicate that (1) no ternary compound was found in this system; (2) the solubility of Fe in the liquid phase of the Co-rich corner at 1300 °C is extremely large; (3) the liquid phase in the Zr-rich corner and the (Co,Fe)₂Zr phase form the continuous solid solutions from the Co-Zr side to the Fe-Zr side; (4) the solubility of Zr in the fcc (Co, Fe) phase is extremely small.     

Redetermination of the eutectic point in the Au-Sb-Si system

Short Communications

Redetermination of the eutectic point in the Au-Sb-Si system