微量元素Y、Ag对Cu基非晶合金玻璃形成能力的影响

采用单辊旋淬法制备了Cu50Zr42Al8,Cu46 Zr47-xAl7Yx(x=2,5),Cu43Zr42AlsAg7和Cu43Zr42Al8Ag5 Y2非晶合金薄带,利用X射线衍射和差示扫描量热分析研究了合金样品的玻璃形成能力和热稳定性.结果表明,在Cu50Zr42Al8中添加适量的Ag、Y后使得非晶合金的短程有序结构发生改变.合金Cu46Zr47-xAl7Yx(x=2,5)的过冷液相区宽度ΔTx分别比Cu50 Zr42 Al8增加了19K、30K,约化玻璃转变温度Trg从0.565分别增加到0.579和0.566,参数γ从0.402分别增加到0.418和0.420,说明Y的添加提高了非晶合金的热稳定性和玻璃形成能力.合金Cu43Zr42 Al8Ag7和Cu43Zr42Al8Ag5Y2与Cu50Zr42Al8相比,约化玻璃转变温度Trg及参数γ均有了明显的提高,达到了0.619、0.416和0.609、0.411,表明Ag的添加、Ag和Y的同时添加均提高了Cu - Zr -Al系非晶合金的玻璃形成能力,但Ag的效果更加显著.     

Zr对Co基合金铸态组织和玻璃形成能力的影响

采用单辊旋淬法制备Co-Fe-Zr-Nb-B多元合金非晶薄带.利用扫描电子显微镜(SEM)、X射线衍射仪(XRD)和差示扫描量热仪(DSC)对样品的微观组织、物相组成及热稳定性进行检测分析,以研究Zr元素含量对其铸态组织和玻璃形成能力的影响.结果表明:在合金中适量添加Zr元素有利于提高铸态组织的细小均匀化程度,同时,合金具有较强玻璃形成能力和较高热稳定性.Zr元素含量为4%(原子分数)时铸态组织最均匀细小,具有很好的非晶形成能力及热稳定性,其玻璃转变温度Tg,初始晶化温度Tx和过冷液相区(SLR)宽度△Tx或(Tx-Tg)分别为870.32、936.28和65.96 K.     

Cu,Co置换Ni对Al-Ni-La非晶合金晶化行为的影响

通过单辊快淬制备了Al85Ni9-xMxLa6和Al86Ni9-xMxLa5(M=Cu或Co,x=0～9)合金的薄带,利用X射线衍射仪(XRD)研究了薄带快淬态和退火态的结构,利用差示扫描量热仪(DSC)研究了上述合金薄带的晶化过程。结果表明,过量Cu,Co置换Ni降低合金的非晶形成能力,形成非晶相和晶态相的混合结构;Cu,Co置换Ni分别促进fcc-Al和亚稳相作为初生相析出:Al85Ni9-xCuxLa6合金的初生相由单独亚稳相MP1逐渐向单独fcc-Al转变,而Al86Ni9-xCoxLa5合金的初生相由单独fcc-Al逐渐向fcc-Al、亚稳bcc-(AlNi)11La3-like相和MP1转变,并趋于析出单独MP1;Cu,Co置换Ni分别降低和提高热稳定性:Al85Ni9-xCuxLa6和Al86Ni9-xCuxLa5合金的晶化开始温度Tx1分别从x=0时的545.5和520.3 K逐渐减至x=8时的415.0 K和x=7时的390.1 K,而Al85Ni9-xCoxLa6和Al86Ni9-xCoxLa5合金的Tx1分别逐渐增至x=6时的592.2 K和x=9时的576.8 K;Cu,Co置换Ni分别减弱和增强玻璃转变:Al85Ni9-xCuxLa6合金的玻璃转变迅速减弱,过冷液相区宽度ΔTx从x=0时的16.5 K逐渐减至x=2时的14.6 K,并于x2时完全消失,Al86Ni9-xCuxLa5合金即使当x=1时玻璃转变也随之消失,而Al85Ni9-xCoxLa6和Al86Ni9-xCoxLa5合金的ΔTx分别从x=0时的16.5和15.4 K逐渐增至x=6时的26.0 K和x=5时的19.9 K。     

Y基非晶合金的形成及晶化动力学

利用单辊急冷法制备Y56-xZrxA124Co20(x=0,5,10)非晶合金,研究Zr含量对该非晶合金的形成能力及热稳定性的影响.研究结果表明,添加元素Zr可以提高Y56A124Co20合金的非晶形成能力和热稳定性,而且随着Zr含量增加,合金的非晶形成能力提高.通过示差扫描量热法(DSC)研究了Y56A124Co20和Y46Zr10A124Co20的晶化动力学,前者的玻璃转变激活能和晶化激活能分别为366.5 KJ/mol和259.7 KJ/mol,后者的玻璃转变激活能和晶化激活能分别为415.6 KJ/mol和319.5KJ/mol,从理论上说明添加元素Zr可以改善Y56A124Co20合金的非晶形成能力和热稳定性.     

Cu75Ni9Sn2P14非晶合金热稳定性的研究

研究了Ｃｕ７５Ｎｉ９Ｓｎ２Ｐ１４合金非晶态结构的形成及其热稳定性。在连续升温的条件下,观察各温度点的晶化情况,发现在１５０℃就有晶相出现,到４００Ｃ时结晶产物均为富铜相。     

过冷处理对Cu45Zr42Al8Ag5非晶热稳定性及力学性能的影响

采用过冷液体等温处理的方法制备出直径为3 mm的Cu45Zr42Al8Ag5合金圆棒,研究了过冷液体等温处理对铜基内生复合材料的热稳定性和力学性能的影响,研究表明,过冷处理后的试样均为原位自生晶体/非晶复合材料,且其有较好的热稳定性.由铜基非晶合金压缩后的应力--应变曲线可以看出,随保温时间的延长,最大抗压强度逐渐降低...     

锆基块体非晶合金力学性能的研究进展

锆基块体非晶合金具有优良的非晶形成能力,可在很小的冷却速率条件下获得.锆基非晶合金具有高强度、超塑性、高弹性、高硬度、高耐磨性和高耐腐蚀性能等,有着广阔的应用前景.总结了锆基非晶合金的形成机制,着重对锆基非晶合金的力学性能、耐腐性能等进行了综述.     

Al-Co-Y合金系非晶的形成及其晶化过程

利用熔体快淬法制备出了Al92-xCo8Yx（x=4,6,8,9,10）薄带,采用X射线衍射（XRD）和扫描电镜（SEM）进行结构分析,示差扫描量热仪（DSC）进行热稳定性分析。研究了Y的加入对合金的非晶形成能力的影响以及Al84Co8Y8合金薄带等温退火的晶化过程。结果表明：当Y的原子分数为8%时,合金系的非晶形成能力最好;非晶态Al84Co8Y8合金的晶化过程分为3个阶段进行,退火过程中的组织结构转变为：非晶合金→非晶基体＋初晶α-Al＋少量未知亚稳相→α-Al相＋未知亚稳相＋Al9Co2→α-Al相＋Al9Co2相＋Al3Y相。     

化学短程序对Al-Zn基合金非晶形成能力的影响

通过X射线衍射和差示扫描量热(DSC),研究了化学短程序对Al-Zn-Ce合金非晶形成能力的影响.结果表明,Ce的加入有利于增加Al-Zn基合金原子间的化合作用,增强化合物形成趋势,阻止相分离.X射线衍射图中的预峰表明了Al-Zn-Ce合金中存在强烈的化学短程序,且化学短程序的存在提高了Al-Zn-Ce合金的非晶形成能力.     

Ce对Al-Ni-Zr合金的非晶形成能力及力学性能的影响

加入Ce部分取代Al84Ni10Zr6合金中的Zr,用单辊旋淬法制备Al84Ni10Zr6-xCex(x=0~6,%)合金,利用X射线衍射、差示扫描量热和纳米压痕等试验分析方法研究Ce取代Zr对Al84Ni10Zr6合金的非晶形成能力及力学性能的影响。结果表明,用Ce代Zr可有效抑制α-Al、Al3Ni等初生晶体的形成,提高合金的非晶形成能力、显微硬度和弹性模量。x=0时,Al84Ni10Zr6合金具有完全晶体结构,显微硬度和弹性模量都较低。x=1~5时,合金具有晶体+非晶复合结构,增加Ce含量,则初生晶体相减少,合金的显微硬度和弹性模量提高。x=6时,Al84Ni10Ce6合金具有完全非晶态结构,显微硬度和弹性模量最高,分别达到4.29和94.99 GPa。x≥3时,合金出现明显的玻璃转变现象,过冷液相区ΔTx为11~16 K,约化玻璃转变温度Trg为0.46~0.48。     

机械合金化制备Co80Zr20非晶合金粉末

采用行星式高能球磨机，通过室温下球磨纯元素混合粉末制备出原子数分数比为Co80Zr20的非晶合金粉末。应用X射线衍射（XRD）、差示扫描量热分析仪（DSC）、扫描电镜及透射电镜对不同球磨时间的混合粉末进行了研究。结果发现，球磨时间对混合粉末的结构及颗粒形貌存在显著影响。原始混合粉末由密排六方的β-Co和α—Zr组成，经过0．5h球磨，β—Co转变为同素异构的面心立方的α—Co，随着球磨时间的增加，Co、Zr颗粒都发生严重塑性变形，并且通过冷焊团聚起来，形成具有层状结构的复合颗粒。球磨导致基体元素Co品格中的晶体缺陷密度大大增加，使得合金元素Zr原子向Co品格中扩散迁移，扩散迁移到Co晶格中的Zr原子数量随球磨时间的增加而增加，导致Co元素的品格常数单调增大。当球磨时间达到8h时，形成Co80Zr20固溶体，继续球磨至10～20h，固溶体转变为非晶。球磨20h得到的非晶粉末的玻璃化转变温度为759K，它可以在840K通过单一放热过程或者继续球磨至40h而发生晶化反应，这两种不同晶化工艺所得到的晶化产物完全相同，均为面心立方的Co23Zr6。     

The Effects of Sc Alloying in Y56Al24Ni10Co10 Glasses on the Local Atomic Structure

Using neutron diffraction and the pair density function analysis, the effect of Sc alloying for Y on the local atomic structure of Y_56-x Al₂₄Ni₁₀Co₁₀ was investigated. The replacement of Y with Sc significantly changes the local atomic structure of amorphous Y_56-x Al₂₄Ni₁₀Co₁₀ as it promotes the formation of nanocrystalline particles. By comparing the structure function in reciprocal space of three alloys with x = 0, 0.1, and 0.2 (in atomic percent), small Bragg peaks are observed that increase in intensity proportionate with the amount of Sc. In real space, the substitution of Sc for Y leads to a drastic structural contraction most likely resulting from efficient cluster packing.     

Spray forming of bulk Al85Y8Ni5Co2 with co-existing amorphous, nano- and micro-crystalline structures

A 12 mm thick Al₈₅Y₈Ni₅Co₂ plate was spray deposited on a 30 mm thick pre-heated copper substrate. The deposit was characterized using optical, high resolution scanning and transmission electron microscopy. Differential scanning calorimetry was performed to assess the crystallization behaviour of the deposit compared to melt spun ribbons of the same composition. The deposit shows an amorphous phase fraction of 83 and 56 vol.% (based on the total crystallization energy), in the bottom and top regions of the deposit. The deposit consists of amorphous and nanoscale structures along with microcrystalline intermetallic phases. The large amorphous phase fraction in the deposit is attributed to the chilling effect upon deposition of highly undercooled/partially crystallized droplets onto the pre-heated substrate and rapid heat extraction thereof due to bonding at the deposit/substrate interface.     

Effect of yttrium on thermal stability and crystallization behavior of Nd60Fe20Al10Ni10 amorphous alloys

The effect of yttrium on the thermal stability and crystallization behavior of Nd-Fe-Al-Ni amorphous alloys was investigated using X-ray diffraction （XRD）, differential scanning calorimeter （DSC）, and transmission electron microscopy （TEM）.The results indicated that the as-cast Nd60Fe20Al10Ni10-xYx（X=-0, 2） amorphous alloys were fabricated with some quenched-in crystals, which could be restrained by Y. With the effect of yttrium, both the crystallization temperature and exothermic peak shifted to higher temperatures, illustrating that the thermal stability could be improved. The addition of Y changed the crystallization process and final crystallization results. Moreover, the crystallites in the amorphous matrix became more homogeneous and smaller. Meanwhile, Y was useful for the passivation of oxygen in chemistry and restrained the negative effect of oxygen. The activation energies of the start of crystallization and peaking were 1.21 and 1.16 eV, respectively, according to the Kissinger equation.     

Influence of crystallization on corrosion resistance of Al86Ni6La6Cu2 amorphous alloy

The influence of crystallization on the corrosion behavior of Al86Ni6La6Cu2 amorphous alloy in 0.01 M NaCl solution was investigated by electrochemical techniques. The Al86Ni6La6Cu2 amorphous alloy was prepared by melt spinning method, and the partially and fully crystallized states were obtained by controlled annealing. The evolution of the crystallization process after annealing was characterized by differential scanning calorimeter （DSC） and X-ray diffraction. The polarization curves revealed that all samples exhibited spontaneous passivation. The fully amorphous Al86Ni6La6Cu2 sample exhibited the best corrosion resistance. Partial and full crystallization resulted in deterioration of corrosion resistance in comparison with that of the as-spun amorphous state.     

Nucleation and growth modes deduced from particle density distributions: Nanocrystallization of fcc Al in amorphous Al85Ni8Y5Co2

A general model to simulate the particle density distribution of a product phase upon phase transformation has been developed in a modular way. In particular, the influence of different nucleation and growth mechanisms known from solid-state phase transformations on the shape of the product phase particle density distribution has been investigated. The model has been fitted to experimental particle density distributions of nanoparticles of fcc Al developing in amorphous Al₈₅Ni₈Y₅Co₂ upon annealing for different times (1 minute to 2 hours) at various temperatures (473 to 508 K). Transient nucleation at a limited number of favored nucleation sites in combination with a two-stage growth mechanism (interface-controlled growth in the beginning and volume diffusion-controlled growth in the subsequent growth stage) very well describes the nanocrystallization process of amorphous Al₈₅Ni₈Y₅Co₂.     

Full or partial replacement of Y by rare-earth and some other elements in the Al85Y8Ni5Co2 alloy

The present paper aims to report the effect of partial or full replacement of Y in the Al₈₅Y₈Ni₅Co₂ alloy by other rare-earth (RE) metals. Influence of small amount of Zr, Pd or Cu additions was also studied for comparison as these elements also have a negative heat of mixing with Al. The studied alloys were produced by rapid solidification of the melt. Glass-forming ability, crystallization behaviour and stability of the supercooled liquid have been studied by X-ray diffraction (XRD) and differential scanning calorimetry (DSC). It has been found that additions of RE metals have not caused critical changes of the properties of the Al₈₅Y₈Ni₅Co₂ alloy while small amount of Pd or Cu additions significantly change its crystallization behaviour and destabilize the supercooled liquid. Addition of more than about 3 at.% of Zr causes precipitation of the primary Al₃Zr phase during rapid solidification.