冷却速度对过共晶A1-Si合金的初晶Si微细化的影响

通过检测过共晶Al-20%Si-1%Cu-0.5%Mg-0.5%Mn合金不同变质处理下的组织变化,研究了冷却速度对初晶Si微细化的影响,结果表明：在5－100℃/s的不同冷却速度下,未变质合金的初晶Si粗大,为50－120μm,冷却速度对初晶Si尺寸的影响较显著,磷变质或双重变质条件下,冷却速度的变化对初晶Si细化的影响较小,双重变质剂具有同时细化共晶Si及初晶Si的作用,使初晶Si比磷变质更细小,可使初晶Si小于20μm。     

细化、变质剂Al-Ti-C-Sr中间合金的制备及效果研究

采用二步法制备Al-Ti-C-Sr中间合金,预制AI-10Sr铝熔体温度850℃,用纯氩气精炼。采用自蔓延法预制Al-Ti-C铝液,氟钛酸钾和石墨粉加入熔体的温度为800℃-900℃,并在最终使熔体达到1200℃以上。合成Al-Ti-C-Sr中间合金是在Al-Ti-C熔体温度在800℃-900℃时加入AI-10Sr合金。再用制备好的Al-Ti-C-Sr中间合金对A356铝合金进行细化变质处理,具有细化和变质双重作用,效果明显。     

铝硅合金变质的研究进展

综述了当前国内外铝硅合金变质处理及其变质机理的研究进展。变质元素Na、Sr、Sb、Ba、Te、Bi、P、S、Ca、As、稀土等已取得了良好的变质效果,通过对比分析其变质机理以及绿色无污染、经济长效等方面的优缺点,比较了这些变质元素单一变质、二元变质和多元变质的优势与局限性,并展望了铝硅合金变质方法的发展趋势。     

中间合金细化剂在铝合金中的应用及细化机理

摘要：综述了中间合金细化剂对铝合金晶粒细化处理的研究与应用现状。对已开发的Al—Ti—B，Al—Ti—C，Al—Ti—C-B和Al—Ti—B-RE等新型的中间合金细化剂进行了详细的比较。并对具有代表性的细化理论如包晶反应、碳化物一硼化物及组织遗传性进行了分析和讨论。但迄今还没有一种观点和理论能完全解释所有的晶粒细化现象和细化行为。     

亚共晶Al—Si合金细化及变质的研究现状与发展

本文介绍了亚共晶Ａｌ－Ｓｉ常用的细化剂和变质剂,分析和概括了现有的一些细化理论,如“包晶反应”、“颗粒理论”、“晶体增殖理论”、“超形核理论”,以变质理论,并简要讨论了化学细化法制备半固态亚共晶Ａｌ－Ｓｉ合金。     

一种复合强效变质剂对亚共晶Al－Si合金组织及性能的影响EI

本文通过所研制的复合变质剂对新型亚共晶铝硅合金进行变质处理，α－Ａｌ晶粒明显变细，分布均匀，分叉率增加。共晶硅尺寸减小，分枝增加，并可在熔拣温度下保温４ｈ或重熔５次以上仍保持变质效果。经变质后的组织为共晶硅粒状化处理创造了有利条件，使铝硅合金的综合力学性能明显提高。     

变形Al-Sr中间合金的变质遗传效应

经变形处理后的Al－5％Sr中间合金与未变形的相比,具有明显的变质效果差异在砂型条件下,用Al－5％Sr中间合金对共晶Al－Si合金进行变质处理,加入含锶量为0．1％的锭料,变质度为5级;加入变形处理的中间合金时,含锶量仅为0．05％时变质度为5级,含锶量为0．06％即达到最佳变质效果,为5.5级在金属型条件下,加入含锶量为0．06％的锭料与加入含锶量0.03％的变形处理的中间合金的变质效果相当,都为6级这种变质效果的差异是Al－5％Sr中间合金的组织遗传效应造成的     

AlTiC中间合金组织遗传性的研究

详细论述了采用不同铸造工艺制取的相同成分不同组织形貌的AlTiC中间合金。通过对比试验发现,不同组织形貌的AlTiC中间合金细化工业纯铝时具有明显不贩细化效果,AlTiC呈块状分布的AlTiC中间合金细化效果最好,其次是TiAl3呈梅花状和片状分布的AlTiC中间合金。借助金相显微镜、X射线衍射仪手段对其组织进行了分析对比,探讨了组织遗传对细化效果的影响,分析表明：3种AlTiC中间合金的相组织相同,均由αAl基体、TiAl和TiC组成,细化效果的差异由AlTiC中间合金的组织遗传效应造成的。     

变质剂对高硅铝合金标准样品组织均匀性的影响

采用金相观察和X射线衍射分析方法研究了Al-Sr,Al-P,Cu-P三种变质剂对高硅(22%,质量分数)铝合金标准样品组织均匀性的影响.结果表明:未添加变质剂的标准样品中初晶硅呈粗大板片状,且局部聚集成团,组织均匀性差;添加了Al-Sr变质剂后初晶硅得到了一定的细化,但共晶硅高度分枝,组织分布仍不够均匀;添加Al-P和Cu-P变质剂后,标准样品中出现了新相AlP,使得初晶硅由板片状变成了细小的多边形颗粒,且弥散分布于整个基体中,同时共晶硅析出明显减少,而初晶硅数量增多,标准样品的组织均匀性好.另外对比发现,添加Cu-P变质剂后的改善效果最为显著,组织均匀性最好,且其成分均匀性通过传统的极差法检测也完全符合标准样品的要求.本工作从组织均匀性上为高硅铝合金标准样品的制备提供了新的判据和参考.     

Sr变质对Al—Si合金共晶硅中孪晶产生的影响

本文利用TEM观察了经Sr变质后Al-Si合金中共晶硅的生长特征。结果表明:变质后共晶硅中孪晶密度较高,且常有两个以上的{111}孪晶同时存在,生长速度对孪晶密度与孪晶特征影响很大。文章也分析了产生上述现象的原因。     

Zr对过共晶铝硅合金中初生硅组织的影响

采用金相显微镜、扫描电镜、X射线衍射仪等实验手段,研究了质量分数为1%、3%和5%的Zr对Al-20Si铝合金铸态组织的影响。结果表明,随着Zr质量分数的增加,初生硅颗粒尺寸逐渐变大。加入Zr后,反应生成了AlSi4Zr5,毒化了形核核心,使晶粒长大;同时Zr使初生硅周围分枝状的α-Al"晕圈"形成充分,减小了对初生硅生长的抑制。     

电磁搅拌对过共晶Al-Si合金初生Si长大过程和形貌的影响

研究了电磁搅拌对过共晶Al-Si合金中初生Si长大和形貌的影响。结果表明,当合金含Si量低于30％时,电磁搅拌引起过共晶Al-Si合金中初生Si显著细化和球团化,但当合金含Si量超过30％时,电磁搅拌对初生Si细化的作用有限,组织中仍然存在较粗大的板片状初生Si;提高电磁搅拌时合金熔体冷却速度可减小初生Si的尺寸;进行正、反转电磁搅拌,初生Si的尺寸将进一步减小,在电磁搅拌条件下,初生Si发生细化和球团化的主要原因是：搅拌引起合金熔体温度场、溶质场的均匀化,引起初生Si的机械破碎,相互摩擦和抑制初生Si各向异性生长。     

Al-17Si-xLa合金室温阻尼-应变振幅行为研究

研究了过共晶Al-17Si-xLa合金在室温下不同频率的阻尼一应变振幅行为。Al-17Si-xLa合金通过常规的铸造和喷射成形工艺制备,并采用动态热机械分析仪(DMTA)对其阻尼行为进行研究。结果表明大多数铸态以及喷射成形态Al-17Si-xLa合金显示了类似的室温应变振幅-阻尼行为：即随振幅的增加,阻尼先不增大,然后明显升高出现阻尼峰,最后回落,可以用G-L位错阻尼理论加以解释;铸态下添加La对Al-17Si合金的阻尼行为影响不大,过量La(6％(质量分数))添加明显降低阻尼性能。La的添加明显提高喷射成形态Al-Si合金阻尼性能。喷射成形态Al-Si合金的阻尼明显比相应铸态Al-Si合金的阻尼高。     

Internal stress and solid solubility effects on the thermal expansivity of Al-Si eutectic alloys

Thermal expansion measurements are reported for a number of as-cast Al-Si eutectic alloys including a Sr-modified alloy which gives nearly spherical Si particles. The measurements were obtained by heating and cooling over repeated temperature cycles between room temperature and 500°C. In general, lower expansivity values were measured on the cooling cycle as compared with the heating cycle, resulting in a net positive permanent deformation at room temperature. Analytical solutions are described for the thermal expansivity of a concentric-spheres model for a Si particle contained within an Al matrix. The effect of plastic flow in the Al is included. Overall, the predictions show reasonable agreement with the measured expansivities. The observed differences between heating and cooling are of the same order as that which is predicted. At high temperatures, the measured increase in expansivities is smaller than calculated. The latter effect is explained by the decrease in expansivity which results from an increasing solid solubility of silicon in aluminum with increasing temperature.Paper presented at the Ninth International Thermal Expansion Symposium, December 8–10, 1986, Pittsburgh, Pennsylvania, U.S.A.     

Effect of addition of Al-Si eutectic alloy on microstructure and mechanical properties of Mg-12wt%Li alloy

Mg-12Li, Mg-12Li-3(Al-Si), Mg-12Li-7(Al-Si) and Mg-12Li-9(Al-Si) alloys (all in wt%) were fabricated by high frequency vacuum induction melting in a water cooled copper crucible. After subsequently hot-rolling and annealing, their microstructure and mechanical properties were investigated. Experimental results show that mechanical properties of Mg-12Li alloy were significantly improved by the addition of Al-Si eutectic alloy. Mg-12Li-7(Al-Si) alloy shows the highest strength of 196 MPa of the investigated alloys, which is about 1.8 times of the strength of Mg-12Li alloy, and maintains high elongation of 27%. The improved mechanical property with addition of Al and Si in the eutectic proportion into Mg-12Li alloy was attributed to the solution strengthening effect of Al and precipitation hardening effect from AlLi and Mg₂Si precipitates.     

Characterization of high-pressure die-cast hypereutectic Al-Si alloys based on microstructural distribution and fracture morphology

The fracture behavior of high-pressure die-cast hypereutectic (HPDC) Al-Si alloys was investigated using a high-resolution laboratory CT and synchrotron X-ray tomography with a particular focus on the influence of HPDC microstructure. Results showed that microstructure of the alloy was mainly comprised of primary silicon particles (PSPs), Al dendrites, Cu-rich phases and pores. Most of the coarse PSPs, Cu-rich phases and pores were located in the center of the specimen. The rapid solidification of HPDC led to a heterogeneous microstructural feature. Elemental Cu was enriched in the frontiers of solid-liquid interface, causing the formation of large size dendritic arms. The pores were formed in the interdendrites which endured high stress intensity under high applied stress. Microcracks were originated from pores and further connected Cu-rich phases causing intergranular fracture. PSPs worked as obstacles causing piling-up dislocations in the phase interface. In the regions where large size of PSPs enriched in, PSPs ruptured rather than debonded from matrix, indicating transgranular fractures of PSPs. Microcracks originated around pores and PSPs tended to converge on the main cracks to decrease the energy required for crack propagation.