深过冷Al72Ni12Co16合金熔体中的相选择

采用惰性形核涂层型壳和氩气保护下循环过热的方法，使Al72Ni12Co16合金获得200K的大过冷度，在此基础上从实验和理论两方面研究了深过冷Al72Ni12Co16合金熔体中的相选择规律。实验和理论计算表明：熔体过冷度是决定Al72Ni12Co16合金中准晶相与晶体相竞争形核的主要因素，且存在一临界过冷度，其值约为60K，当Al72Ni12Co16合金的初始过冷度大于临界过冷度时，十面体准晶相将作为初生相从熔体中析出；反之，当Al72Ni12Co16合金的初始过冷度小于临界过冷度时，熔体初生相为β晶体相。     

快速凝固Mg80Cu10Y10金属玻璃的晶化行为

采用单辊快速凝固法制备了Mg80Cu10Y10合金薄带,并对合金薄带进行热处理,利用XRD、DSC和HRTEM分析研究了该合金薄带的晶化过程及其晶化后的微观结构.结果表明:快速凝固Mg80Cu10Y10合金薄带为单一的非晶态结构,其约化玻璃转变温度Trg为0.62,具有较强的非晶形成能力;非晶合金具有三阶段晶化行为;在热处理温度为423 K时合金仍为非晶态;当温度达到473 K时,合金发生明显晶化,在非晶基体上弥散析出Mg2Cu、Cu2Y和hcp-Mg纳米晶粒;随着温度由523 K升高至623 K时,析出晶粒尺寸增大、数目减少,合金中的晶体相为hcp-Mg、Mg2Cu和Mg24Y5.     

Mg_(80)Cu_(15)Y_5合金的非晶形成能力及晶化行为

采用单辊快速凝同法制备出厚约40μm的Mg_(80)Cu_(15)Y_5非品合金薄带,利用XRD、DSC、TEM和HRTEM研究了非品合金的非品形成能力和晶化行为,分析了品化对合金组织结构与性能的影响.结果表明:Mg_(80)Cu_(15)Y_5合金的过冷液态温度区间△T_x和约化玻璃转变温度T_(rg)分别为55K和0.58,表明其具有较强的非晶形成能力;该合金在退火温度高于473 K后发牛明显晶化,从非品基体中析出 Mg_2Cu、Cu_2Y和Mg晶体相;随着退火温度的升高,合金的硬度呈现出先升高后降低的变化趋势,这与纳米品体相颗粒的弥散析出、重溶及粗化有关.     

预退火时间与Fe68Ni1Al5Ga2P9.65B4.6Si3C6.75玻璃转变热力学参数的关系

采用DSC、XRD 检测方法,分析了经673 K((Tg-100 K)＜T＜Tg)不同时间(20,40,60 min)预退火处理后,Fe68Ni1Al5GazP9.65B4.6Si3C6.75非晶合金的玻璃转变温度Tg、起始晶化温度Tx、晶化峰温度Tp、玻璃转变过程中的比热容增量△Cp,g的变化以及经823 K晶化反应后的XRD图谱.结果表明:Fe68Ni1Al5Ga2P9.65B4.6Si3C6.75非晶合金的玻璃转变温度Tg和比热容增量△Cp,g随预退火时间的延长而逐步增加;起始晶化温度Tx和第一晶化峰温度Tp1随预退火时间呈现出逐渐减小的趋势;其晶化后样品衍射峰形貌相似,衍射峰的强度略有不同.利用结构弛豫理论对实验结果进行了分析.     

电脉冲孕育处理对Zr基块体非晶热稳定性及退火晶化的影响

通过先对Zr55Ni5Al10Cu30合金熔体施加脉冲电流处理,再利用非真空吸铸法制备出Zr55Ni5Al10Cu30块体非晶合金的方式,研究了电脉冲孕育处理对非晶热稳定性及退火晶化的影响。差分扫描量热(DSC)及X射线衍射(XRD)分析结果表明:经电脉冲孕育处理后Zr55Ni5Al10Cu30块体非晶合金的玻璃转变温度上升,晶化温度降低,过冷液相区变窄,同时玻璃转变激活能和晶化激活能有所减少。电脉冲孕育处理没有改变Zr55Ni5Al10Cu30块体非晶合金退火晶化相演变过程,但提高了非晶退火晶化率。电脉冲孕育处理对Zr55Ni5Al10Cu30块体非晶合金的晶化起到了促进作用。     

Fe_(77)Co_4Zr_9B_(10)合金的热稳定性、微观结构和磁性能研究

采用单辊快淬法制备Fe77Co4Zr9B10非晶合金,在不同温度下对该合金进行热处理。利用差热分析仪(DTA)、X射线衍射仪(XRD)、原子力显微镜(AFM)以及振动样品磁强计(VSM)等手段对Fe77Co4Zr9B10合金薄带的晶化行为、微观结构和磁性能进行研究。结果表明:Fe77Co4Zr9B10非晶合金的晶化峰值温度Tp的晶化激活能Ep为525.19 k J/mol。Fe77Co4Zr9B10非晶合金在晶化初期,观察到α-Fe和α-Mn型晶化物析出;943 K退火,α-Mn型晶化物消失。Fe77Co4Zr9B10合金在晶化初期,α-Mn型晶化物的析出导致矫顽力(Hc)恶化;在943K退火后,Hc的下降与α-Mn型晶化物的消失和α-Fe相体积分数的增加有关。     

La-Y-Ni系A5B19型退火合金的相结构和电化学性能

采用真空电弧熔炼和热处理制备了A5B19型储氢合金La0.4Y0.6Ni3.52Mn0.18Al0.1,研究了退火温度(1173～1373 K)对合金La0.4Y0.6Ni3.52Mn0.18Al0.1相结构和电化学性能的影响规律.结果表明,随退火温度增加,主相A5B19型(3R-Ce5Co19+2H-Pr5Co19)...     

非晶合金的晶化动力学与初生相的内在联系

通过差示扫描量热法(DSC)研究了Zr60Al15Ni25非晶合金的晶化动力学。X射线衍射(XRD)和能谱(EDS)分析结果表明:Zr60Al15Ni25非晶合金晶化过程中的初生相为复杂三元化合物Al2NiZr6和AlNi4Zr5。非晶合金的有效晶化激活能反映了晶化初生相与非晶相间的结构差异,二者结构差异越大,有效晶化激活能就越高,Zr60Al15Ni25非晶合金的有效晶化激活能高达345 kJ/mol;当合金高温熔体快冷过程中的初生相与非晶合金的晶化初生相一致时,晶化动力学参数能够实际反映合金的玻璃形成能力,相反则不能。     

(Al100-x Bex)85 Gd8Ni7(x=0～8.4)合金的玻璃形成能力和初晶化

研究了Be部分替代Al对Al85Gd7Ni8合金的玻璃形成能力和初晶化的影响.结果表明,当Al-Be-Gd-Ni合金中Al/Be比例为二元Al-Be系的固溶成分时,即(Al99.75 Be0.25)85 Gd8Ni7,合金表现出最佳的玻璃形成能力和力学性能;一定的Be替代Al(x=0.25与x=1)升高初始晶化温度,抑制金属间化合物的析出,有利于获得高密度α-Al弥散分布于非晶基体的复合结构.     

(A1_(l00-x)Be_x)_(85)Gd_8Ni_7(x=0～8.4)合金的玻璃形成能力和初晶化

研究了Be部分替代Al对Al85Gd7Ni8合金的玻璃形成能力和初晶化的影响。结果表明,当Al-Be-Gd-Ni合金中Al/Be比例为二元Al-Be系的固溶成分时,即(Al99.75Be0.25)85Gd8Ni7,合金表现出最佳的玻璃形成能力和力学性能;一定的Be替代Al(x=0.25与x=1)升高初始晶化温度,抑制金属间化合物的析出,有利于获得高密度α-Al弥散分布于非晶基体的复合结构。     

Crystallization and microstructure evolution of amorphous Al85Y4Nd4Ni7 alloy

The mixture model of Al85Y4Nd4Ni7 alloy in which a partially crystallized amorphous alloy is regarded as a nanocomposite of an Al nanoparticle and a remaining amorphous matrix is presented. Its evolution in the process of crystallization has been investigated by differential scanning calorimetry (DSC), X-ray diffraction (XRD), and transmission electron microscopy (TEM). Mainly amorphous structure with α-Al nanocrystals embedded in the amorphous matrix has been revealed by melt spining the alloy. Crystallization is showed to occur in three stages: (I) crystallization of amorphous alloy and formation of A1NiY, A1NdNi and unknown crystalline phases, (2) formation of Al3Y and Al3Nd, and (3) formation of Al3Ni.     

非晶态铝合金晶化过程的形核与长大行为研究

制备了一种具有较宽过冷液态温度范围（△T=17K）的非晶态Al85Ni5Y8Co2（原子分数）合金。利用差热分析、电阻测量及高分辨电镜监测了合金化动力学过程。结果表明，在非晶态铝合金的退火过程中纳米Al粒子的形核与长大过程是可分离的，即首先发生淬态Al晶核的长大，之后在过冷液态温区发生高密度纳米Al粒子的形核，最终是Al晶核 的长大过程。     

喷射成形La62Al15.7(Cu,Ni)22.3块体非晶合金的晶化行为

研究了喷射成形和铜模吸铸法制备的La62Al15.7(Cu,Ni)22.3块体非晶合金的晶化行为。结果表明,两种工艺制备的非晶合金晶化过程都为三级晶化,晶化的顺序为:非晶→非晶+La→非晶+La+Al3La→非晶+La+Al3La+富Cu和Ni的未知相。结合晶化动力学计算和退火晶化实验结果表明,低温(<503K)时,喷射成形La62Al15.7(Cu,Ni)22.3非晶合金的热稳定性优于铜模吸铸La62Al15.7(Cu,Ni)22.3非晶合金,高温(>553K)时结果相反。     

Al_(80)Ni_6Y_8Co_4Cu_2 GLASS ALLOYS CONTAINING NANOSCALE PARTICLES BY ISOTHERMAL ANNEALING OR QUENCHING

1. IntroductionPartial nanocrystalline Al-rich glajssy alloys have attracted great attention as a newmaterial because their specific strength are much higher than that of the fully amorphousAl-rich alloys and the conventional crystalline Al-based alloy[1,2]. Kim et al.I2] and Chenet al.13] reported that the values of fracture strength are above 1000MPa for Al-rich alloyswith mixed structure of nanoscale or-Al particles embedded on the amorphous matrix afterpartial crystallization. However,…     

Stability of amorphous Al90TMxCe10—x（TM=Fe or Ni） alloys

X-ray diffraction(XRD) and differential scanning calorimetry(DSC) were used to investigate the crystallization process of amorphous Al90TMxCe10-x (atom fraction in%;TM=Fe or Ni;x=3,5)alloys,Aging effects were examined by X-ray diffraction,The structure corresponding to the prepeak for the amorphous Al90Fe5Ce5 alloy is more stble than the amorphous matrix,but it is not stable for amorphous Al90Ni5Ce5 alloy during the first crystallization stage and even decomposes at room temperature,Although both Al-Ni and Al-Fe have strong chemical bonding,the cyrstallization onset temperature of amorphous Al-Fe-Ce alloys is much higher than that of amorphous Al-Ni-Ce alloys,which is likely caused by the different stability of the structure corresponding to the prepeak.The crystallization onset temperature increases as Ce/Ni ratio increases in amporphous Al90NixCe10-x alloys,whereas it decreases as Ce/Fe ratio increases in amorphous Al90FexCe10-x alloys.A better atomic packing produces as Ce content increases because of the size mismatch in Al-Ni-Ce systems and as Fe content increases because of the increasing Fe central structural units.     

Effects of TM on stability of structure corresponding to prepeak of amorphous Al_(90)TM_5Ce_5 Alloys

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快速凝固制备La2Mg0．9Ni7．5Co1．5Al0.1贮氢合金的相结构及电化学性能

采用感应熔铸＋退火处理及快速凝固方法制备了La2Mg0．9Ni7．5Co1．5Al0.1贮氢合金。系统研究了快速凝固对合金的相结构、微观组织及电化学性能的影响。XRD分析表明，随着冷却速率的增加，La2Mg0．9Ni7．5Co1．5Al0.1合金的相组成发生了明显变化。退火合金由αLa2Ni7主相（Ce2Ni7型结构）和少量LaNi3相（PuNi3型结构）组成。随着冷却速率的增加，合金中出现LaNi5相（CaCu5型结构）和LaMgNi4（MgCu4Sn型结构）相，且新相的相丰度增加，aLa2Ni7相和LaNi3相的丰度减少。EPMA分析表明，快速凝固方法制备的La2Mg0．9Ni7．5Co1．5Al0.1贮氢合金为柱状晶组织且晶粒细小。合金电极的电化学测试表明，冷却速率对合金的活化性能影响不大。随冷却速率的增加，合金的最大放电容量减少、高倍率放电性能下降。在较低的冷却速率下（5m／s），合金电极的循环稳定性改善不明显，而随着凝固速度的进一步增加（20m／s），合金电极表现出较好的循环稳定性。     

The effect of Si addition on crystallization behavior of amorphous Al-Y-Ni alloy

This article reports the effect of silicon (Si) addition upon the crystallization behavior and mechanical properties of an amorphous AlYNi alloy. An amount of 1 at.% Si was added to a base alloy of Al₈₅Y₅Ni₁₀ either by substitution for yttrium (Y) to form Al₈₅Y₄Ni₁₀Si₁, or by substitution for nickel (Ni) to form Al₈₅Y₅Ni₉Si₁. Differential scanning calorimetry (DSC) of all three alloys showed three exothermic peaks. Comparing the peak temperature for the first exothermic peak, a significant shift occurs toward the lower temperature. This indicates that 1 at.% substitutions of Y or Ni by Si decreases the stability of the amorphous phase. DSC study of these amorphous alloys during isothermal annealing at temperatures about 5–15 K lower than their first crystallization peaks showed that the formation of α-Al nanocrystals via primary crystallization occurred without an incubation period. The Avrami time exponent (n) of the primary crystallization from the amorphous structure was determined to be 1.00–1.16 using the Johnson-Mehl-Avrami (JMA) analysis. This suggested a diffusion-controlled growth without nucleation. However, a DSC study of these amorphous alloys during isothermal annealing at higher temperatures between 585 and 605 K showed a clear incubation period during the formation of the Al₃Ni and Al₃Y intermetallic phases. An n value of 3.00–3.45 was determined using JMA analysis. This suggested that the transformation reaction involved a decreasing nucleation rate and interface-controlled growth behavior. The tensile strength σ_f and Vickers hardness for these amorphous alloys are in the range 1050–1250 MPa and 380–398 diamond pyramid hardness number (1 diamond pyramid hardness number=1 kg/mm²=9.8 MPa), respectively.     

Crystallization studies of Al<Subscript>85</Subscript>Y<Subscript>10</Subscript>Fe<Subscript>5−x</Subscript>Ni<Subscript>x</Subscript> (x = 0, 2.5, 5) alloys

The crystallization behavior of melt-spun A₈₅Y₁₀Fe_5−xN_x (x=0, 2.5, 5) amorphous alloys has been investigated by a combination of differential scanning calorimetry (DSC) and x-ray diffractometry (XRD). XRD traces of these alloys consisted of a single broad peak corresponding to fully amorphous structure. Continuous DSC results showed that, the first crystallization peak temperature of Al₈₅Y₁₀Fe₅ amorphous alloy was about 60 K higher than that of Al₈₅Y₁₀Ni₅. The activation energies for the first crystallization peak increased from 210 kJ/mol for Al₈₅Y₁₀Ni₅ to 280 for Al₈₅Y₁₀Fe₅. These results indicate that 5 at.% substitutions Ni by Fe increases the stability of the amorphous phase.