废弃锡合金真空分离回收金属（英文）

以废弃锡合金的回收利用为目标,计算绘制了Sn-Pb、Sn-Sb及Sn-Zn二元合金的气-液相平衡成分图。结果表明:Pb、Sb及Zn能够有效地与Sn分离。以此为指导,对不同成分的Sn-Pb合金、Sn-Pb-Sb合金、Sn-Pb-Sb-As合金、粗Pb合金以及Sn-Zn合金开展真空蒸馏工业化实验研究。实验结果表明:Sn-Pb合金在1323K条件下经真空蒸馏可获得含Pb99%的粗Pb和含Pb≤0.003%的Sn;Sn-Pb-Sb合金经一次真空蒸馏,可得到含Sn量90%、含Pb量≤2%、含Sb量≤6%的粗Sn和含Sn≤2%的粗Pb;粗Sn经过真空蒸馏后,产品中Pb和Bi含量达到Sn锭GB/T 728—2010中Sn99.99A级标准,超过50%的As和Sb得到脱除;Sn-Pb合金在1173 K。体系压力20-30 Pa条件下真空蒸馏8-10 h,得到的产品Zn中含Sn0.002%,Sn中含Zn约3%。     

真空蒸馏Zn-Ni二元合金气−液相平衡研究

在系统压力5～10 Pa、蒸馏温度1173～1423 K条件下,开展Zn-Ni二元合金真空蒸馏实验研究.结果表明:液相中Ni含量(质量分数)由18.21％增至96.05％时,气相中的Zn含量由0增至99.9966％,并且通过实验获得真空蒸馏中Zn-Ni二元合金的气?液平衡(Vapor-liquid equilibriu...     

铅锡合金的真空蒸馏深度脱铅(英文)

采用分子相互作用体积模型计算在777℃时不同Pb含量铅锡合金的活度系数,结果与实验值符合较好。对800～1300℃全成分范围内铅锡合金的活度系数进行预测,为铅锡金真空蒸馏分离提供必要的热力学参数。对两种不同铅含量的铅锡合金进行小型和工业实验,将锡中的铅含量降至0.01%以下。设计全成分范围的铅锡合金真空蒸馏处理流程,对铅含量10%～90%的铅锡合金经真空蒸馏处理后可得到纯度为99.5%的粗铅和铅含量在0.01%以下的精锡。     

粗铅真空蒸馏精炼杂质脱除的热力学(英文)

采用纯物质饱和蒸气压、分离系数和Pb-i系气-液相平衡成分图从热力学上分析粗铅真空蒸馏精炼脱除杂质的可行性。探讨粗铅中常见的杂质铜、锡、银、锌、砷、锑、铋在真空蒸馏精炼过程中的行为规律。结果表明:粗铅低温(923~1023 K)真空蒸馏时,锌和砷挥发进入气相而被除去,大部分锑挥发进入气相而实现与铅的分离,而铋则随铅残留于液相中无法除去。粗铅高温(1323~1423 K)真空蒸馏时,铅挥发进入气相冷凝,铜、锡、银不挥发而富集于残留物中被除去,铅挥发的同时铋也随着铅一起挥发进入气相无法除去。此理论为真空蒸馏脱除粗铅中的杂质提供新的思路,并能有效富集贵金属银等,对粗铅采用真空蒸馏精炼除杂具有一定的指导意义和实用价值。     

金银合金真空分离的理论研究（英文）

为准确预测金银合金真空蒸馏过程中产品成分与温度和压力的关系,并为工业生产参数的设计提供便捷和有效的指导,根据分子相互作用体积模型(MIVM),计算不同温度下金银合金的分离系数(β)和气-液平衡成分。结合气液相平衡(VLE)理论,绘制金银合金真空蒸馏的温度-成分、压力-成分相图。同时,对金、银三相点和金、银蒸气冷凝温度进行计算。理论研究结果表明：随着蒸馏温度的升高,分离系数减小,金在气相中的含量增加;低温对分离金银具有积极效果;在压强1～10 Pa范围内,金、银冷凝温度相差约450 K。     

微量元素Cd对锡基轴承合金SnSb11Cu6组织与力学性能的影响

为了改善锡基轴承合金的承载能力,采用X射线衍射分析、光学显微分析、硬度分析和材料拉伸和压缩试验等分析技术研究微量元素Cd对锡基轴承合金Sn Sb11Cu6的微观组织和力学性能的影响。结果表明:Cd加入合金后,并未改变合金的物相组成。合金中硬质相Sn Sb尺寸减小,数目增多,说明Cd能起到细化Sn Sb相的作用,增强合金的硬度、强度和塑性;同时,Cd溶于Sn形成固溶体能提高合金的硬度和强度,但降低合金的塑性。Cd加入到合金Sn Sb11Cu6中,起到细晶强化和固溶强化的作用。当Cd的含量在0.5%(质量分数)左右时,合金的硬度、强度和塑性同时增加,考虑合金的综合性能,推荐优选的Cd含量为0.5%~1.0%。     

分子相互作用体积模型在真空蒸馏分离Pb-Sb、Pb-Ag和Sb-Cu合金中的应用

基于分子相互作用体积模型(MIVM),使用牛顿迭代方法结合无限稀活度系数实验数据γ∞计算对势能相互作用参数Bij和Bji;然后使用参数Bij和Bji计算Pb-Sb、Pb-Ag及Sb-Cu二元合金体系的活度α和活度系数γ,并与实验值进行比较分析;最后计算Pb-Sb、Pb-Ag及Sb-Cu二元合金体系的气液相平衡组成。气液相平衡组成计算结果表明:活度计算值和实验值吻合较好;Pb-Ag和Sb-Cu体系中的组元均能通过真空蒸馏实现良好分离,而Pb-Sb体系中的组元不能通过一次真空蒸馏实现完全分离。分子相互作用体积模型用于预测二元合金体系的活度及真空蒸馏分离效果具有很高的可靠性,为真空蒸馏分离二元合金提供良好的理论依据。     

锡阳极泥硫化焙烧分离锑

提出一种硫化焙烧处理锡阳极泥分离锑的新工艺,对硫化焙烧过程进行热力学分析,在热力学分析的基础上,系统考察焙烧温度、焙烧时间、黄铁矿配比及焦粉配比对锑挥发率和锡残留率的影响。结果表明:温度升高有利于Sb2O4和Sn O2硫化反应的进行,且在同一温度下,Sb2O4比Sn O2硫化的趋势更强。在黄铁矿配比为30%(质量分数)、焦粉配比为7%(质量分数)、焙烧温度为1323 K、焙烧时间为2 h的条件下,焙砂中的锑含量为2.96%、锡含量为31.98%、锑的挥发率为85.56%、锡的残留率为88.75%,锡阳极泥硫化焙烧分离锑效果较佳。     

锡含量对Bi5Sb钎料铺展性能及抗拉性能影响

在Bi5Sb基体钎料中添加1%～8%Sn,研究锡对Bi5Sb基无铅钎料润湿性能及力学性能的影响.结果表明,在Bi5Sb钎料中添加适量的锡,可使Bi5SbxSn钎料熔点控制在270～280℃左右,与Bi5Sb钎料相比,变化不大,但钎料合金铺展性能和抗拉强度明显提高.当锡含量为8%时,Bi5Sb8Sn钎料合金钎焊铺展性能和...     

铜线材氟硼酸盐高速电镀光亮锡铅及锡铅钴合金

用DL01、DL03作光亮剂,在氟硼酸盐镀液中,改变电流密度和搅拌速度在0.5mm的铜线上,电镀出锡 铅和锡 铅 钴合金镀层。结果表明,在Jc=5～18A dm2,v=47、96、150m min时,Sn与Pb的共沉积属异常共沉积。当Jc>30A/dm2时属正常共析。当镀液中含有Co时促进了Sn的共沉积。     

Application of vacuum distillation in refining crude indium

Vacuum distillation is a technique suitable for low boiling and melting point materials,to remove the heavy and low vapor pressure impurities at low level.As indium has low melting point and high boiling point,it is suitable for refining by vacuum distillation.First,saturation vapor pressure for major elements in crude indium was calculated by the Clausius–Clay Prang equation,which could approximately predict the temperature and pressure during vacuum distillation process.Second,the activity coefficients for In–Cd,In–Zn,In–Pb,In–Tl at 1373 K,and In–Sn at 1573 K were acquired by means of molecular interaction on volume model.Vapor–liquid equilibrium composition diagrams of those above systems in crude indium were drawn based on activity coefficients.These diagrams could estimate the compositions of products in each process during the refinement of crude indium.Finally,1.2–1.6 ton crude indium was used per day when vacuum distillation experiments were carried out,and experimental results are in good agreement with the predicted values of the vapor–liquid equilibrium composition diagrams.     

Experimental Investigation of the Phase Equilibria in the Co–V–Sn Ternary System

The phase equilibria of the Co–V–Sn ternary system at the 900 and 1000 °C sections were investigated experimentally by means of electron probe microanalysis and x-ray diffraction analysis. Seven three-phase regions were found in the isothermal section at 900 °C and six triphase regions at 1000 °C. The Heusler-type ternary compound Co₂VSn was confirmed at 900 °C in the composition ranges of 36.7–57.6 at.% Co and 11.8–20.9 at.% Sn, becoming slightly wider at the higher temperature of 1000 °C. Sn dissolves in α(Co), Co₃V, and σ-Co₂V₃ phases with low solubility. V is almost insoluble in liquid, with solubility of less than 0.5 at.%. The solubility of Co in V₃Sn phase increased with temperature, from 4.4 at.% at 900 °C to 11.6 at.% at 1000 °C.     

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.     

The 260 °C phase equilibria of the Sn–Sb–Cu ternary system and interfacial reactions at the Sn–Sb/Cu joints

The isothermal section of the Sn–Sb–Cu ternary system at 260 °C has been determined in this study by experimental examination. Experimental results show no existence of ternary compounds in the Sn–Sb–Cu system. An extensive region of mutual solubility existing between the two binary isomorphous phases, Cu₃Sn and Cu₄Sb, was determined and labeled as δ. Intermetallic compounds (IMCs) Cu₂Sb, SbSn, and Cu₆Sn₅ are in equilibrium with the δ solid solution. Up to about 6.5 at.%Sb can dissolve in the Cu₆Sn₅ phase, and the solubility of Sn in the Cu₂Sb is approximately 6.2 at.%. Each of the Sb and SbSn phases has a limited solubility of Cu. Only one stoichiometric compound, Sb₂Sn₃, exists. Besides phase equilibria determination, the interfacial reactions between the Sn–Sb alloys and Cu substrates were investigated at 260 °C. Sb was observed to be present in the Cu₆Sn₅ and δ phases, and Sb did not form Sn–Sb IMCs in the interfacial reactions. Moreover, the addition of up to 7 wt% of Sb into Sn does not significantly affect the total thickness of IMC layers. It was found that the phase formations in the Sn–Sb/Cu couples are very similar to those in the Sn/Cu couples.     

Sn-Ce-Me无铅钎料合金活度相互作用系数的计算及应用

采用周模型计算分析了Sn-Ce-Me(Me=Pb、Bi、zn、Sb、Ag、Cu、Cd)三元合金系中，Ce与Sn以及Ce与Me之间的活度相互作用系数。计算结果表明，不仅在Sn-Pb-Ce中，Ce存在“亲Sn”现象，在其它6个三元无铅钎料合金体系中，如Sn-Bi-Ce、Sn-Sb-Ce、Sn-zn-Ce、Sn-Cd-Ce、Sn-Ag-Ce、Sn-Cu-Ce，Ce也同样存在着“亲Sn”现象。其研究结果可为新型无铅钎料的研究提供理论分析依据。     

Phase Equilibria in the Cu-Sn-Sb Ternary System

The phase equilibria in the Cu-Sn-Sb ternary system were investigated by means of electron-probe microanalysis and x-ray diffraction. Firstly, ternary solubilities of η-Cu₆Sn₅, δ-Cu₄₁Sn₁₁, Cu₁₁Sb₃, ε-Cu₃Sb and η-Cu₂Sb, were less than 7 at.% Sb or Sn at 400 °C. Besides, an re-stabilized ternary solubility, Cu₆(Sn,Sb)₅, was detected with a homogeneity range of Cu: 52.9-53.3 at.%, Sn: 28.4-30.9 at.%, and Sb: 15.8-18.7 at.%. Its origin was traced back to high-temperature stabilization of the binary η-Cu₆Sn₅ phase. Thirdly, the metastable phase, Cu₁₁Sb₃, was observed at 400 °C in the Cu-Sn-Sb ternary system; On raising the temperature to 500 °C, the ε-Cu₃Sn phase still retained a large solubility for Sb, at?~?16 at.%, while the ε-Cu₃Sb was replaced by β-Cu₃Sb with a dual-cornered large homogeneity range. Similarly, a ternary homogeneity range of Cu: 83.8-84.9 at.%, Sn: 2.6-6.2 at.%, and Sb: 9-12.5 at.%, was found and deduced to be the high temperature stabilization phase of γ-Cu₁₁(Sb,Sn)₂ at 500 °C.     

Experimental investigation and thermodynamic calculation of the phase equilibria in the Co–Mo–W system

The isothermal sections in the Co–Mo–W ternary system at 600 °C, 800 °C, 1000 °C, 1100 °C, 1200 °C and 1300 °C have been determined using the Electron probe micro-analyzer (EPMA) and X-ray diffraction (XRD) techniques. A thermodynamic assessment of the Co–Mo–W ternary system was carried out by the CALPHAD (Calculation of Phase Diagrams) method. The Gibbs free energies of the liquid and solution phases were described by the subregular solution models, and those of intermetallic compounds were described by the sublattice model. A consistent set of thermodynamic parameters has been derived for describing the Gibbs free energies of each solution phase and intermetallic compound in the Co–Mo–W ternary system. The calculated phase diagrams and thermodynamic properties in the Co–Mo–W ternary system are in good agreement with experimental data.     

Mechanism of changes in composition and mass of phases at two-phase equilibria in binary systems

Calculations have been carried out to determine the composition and mass of two equilibrium phases in binary systems under the effect of temperature. We have considered 99 Pb + (1–99)% Sn alloys, which consist of lead- and tin-based solid solutions, in the temperature range of 183–50°C, as well as 99 Co + (1–99)% Cu alloys, which consist of liquid and solid phases, in the temperature range of 1495–1112°C. It has been shown that, depending on the alloy composition, the mechanism of changes in the composition and mass of the phases can involve the passage of both components either from one solid phase into another (Pb-Sn alloys) or from the liquid phase into a solid one (Co-Cu alloys). The concentration of one of the components, which is conventionally called the first component, in the passing substance diminishes to zero. Then, the other (second) component continues to move in the previous direction, the first component moves in the opposite direction, and the second component replaces the first one in the same amount; i.e., the opposing movement of the components from one phase to the other occurs.