Cu基块体非晶合金的玻璃形成能力、晶化机制及变形诱发的结构和力学性能变化
|
摘要
非晶合金因其独特的机械、物理和化学性能成为极具应用潜力的先进材料。然而,合金玻璃形成能力的表征仍然是非晶研究领域未解决的关键问题,现有的各种表征方法都无法解释一些例外的情况。传统快淬薄片非晶至少有一维方向的尺寸很小,室温变形时获得的应变极其有限,限制了在不同应变量下微观结构及性能变化的研究,而块体非晶合金的出现使得室温下的大塑性变形成为可能,为该研究创造了条件。本文基于非晶合金形成过程的热力学和动力学,对非晶形成能力的本质进行了探讨。综合利用X射线衍射仪(XRD)、差示扫描量热仪(DSC)和高分辨透射电子显微镜(HRTEM)分析了Cu_(60)Zr_(20)Ti_(20)块体非晶合金在等温和连续加热退火过程中的晶化机制,考察了Cu_(60)Zr_(20)Ti_(20)和Cu_(47.5)Zr_(47.5)Al_5块体非晶合金在轧制变形到不同应变量时的自由体积和微观结构,并测量了其显微硬度,由此阐明了它们随轧制温度、应变速率和应变量的变化规律,以及它们之间的关联特性,为块体非晶合金的成分设计和非晶基复合材料的开发提供新思路。
在综合考虑非晶形成热力学和动力学的前提下,提出表征玻璃形成能力的新判据,即T_k /T_l ( T_k -Kauzmann温度, T_l -合金液相线温度)和D(合金液体的脆性参数)。研究发现单独在强液体特性的合金或脆液体特性的合金中, T_k /T_l可以很好地表征合金的玻璃形成能力, T_k /T_l越大,玻璃形成能力越好,并且D值的改变并不影响T_k /T_l的表征作用。同时,在对这两类合金的玻璃形成能力进行比较时,发现当T_k /T_l相等时,D值越大,玻璃形成能力越高。
Cu_(60)Zr_(20)Ti_(20)块体非晶合金的晶化过程为两阶段晶化,第一个晶化反应为初生型晶化,析出纳米尺寸的Cu_(51)Zr_(14)相,第二个晶化反应为共晶型反应,析出晶化相为Cu_(51)Zr_(14)和Cu2ZrTi。时间关联形核过程存在于Cu_(60)Zr_(20)Ti_(20)非晶合金的初生晶化和剩余非晶的晶化过程中。Cu_(60)Zr_(20)Ti_(20)非晶合金在过冷液相区等温晶化时初生Cu_(51)Zr_(14)相的形核激活能不仅与等温退火前的加热速度有关,加热速度越快,形核激活能越小,而且还与孕育期起始点算法有关。但是有效晶化激活能与加热速度和孕育期起始点算法无关。
Cu_(60)Zr_(20)Ti_(20)块体非晶合金在室温和150 K低温轧制过程中获得的最大应变量均高达97%,且大变形后的样品仍具有很好的韧性。对应于每一种变形工艺都存在着一个临界应变量,低于这个临界应变量,样品中只有剪切带产生,高于这个应变量,则有相变发生。无论是提高轧制温度还是提高应变速率,发生相变的临界应变量都下降。相变类型都从单纯的相分离向同时发生相分离和纳米晶化的方向转变,并且相分离后的非晶成分更加偏离合金原始成分。Cu_(60)Zr_(20)Ti_(20)块体非晶合金在150 K低温进行轧制时,如果应变速率ε&= 1.0×10~(-4) s~(-1),试样在轧制到最大应变量97%时仍保持单一非晶状态。当ε& = 5.0×10~(-4) s~(-1)时,试样在应变量ε大于93%时发生相分离。提高ε&至5.0×10~(-3) s~(-1)时,发生相分离的临界应变量降低到89%。在更大的应变速率5.0×10~(-1) s~(-1)下,在ε> 67%时就同时发生相分离和纳米晶化。固定应变速率ε&= 5.0×10~(-3) s~(-1),提高轧制温度到室温,试样在ε> 87%也同时发生相分离和晶化。轧制后的试样只有剪切带而没有相变发生时,非晶合金的热稳定性没有明显变化。相分离一旦出现则会降低非晶合金的热稳定性和退火时的晶化激活能。如果相分离和晶化同时发生,合金的热稳定性和晶化激活能会进一步降低。
在Cu_(60)Zr_(20)Ti_(20)块体非晶合金低温、低应变速率的轧制过程中观察到了单一非晶状态下自由体积在高应变量下的饱和现象。提高应变速率,自由体积在变形初期的增加速度、单一非晶合金试样中自由体积达到饱和的临界应变量以及饱和自由体积含量也随之上升。虽然自由体积饱和的临界应变量随应变速率的上升而上升,但是相变发生的临界应变量却随之下降,这两个临界应变量之间的竞争决定了塑性变形过程中自由体积含量能否在样品还是单一非晶相时达到饱和。剪切带中自由体积崩溃成纳米空洞是导致自由体积饱和的根本原因。相分离的出现并不明显改变自由体积含量,但是晶化的发生使自由体积含量降低。
应变速率为5.0×10~(-3) s~(-1)的298 K室温和150 K低温轧制变形都没有导致Cu_(47.5)Zr_(47.5)Al_5非晶样品发生相分离或晶化,只是在靠近剪切带的非晶基体上,出现了原子尺度的成分结构不均匀性。应变量在从0到最大值97%的变化过程中,自由体积含量持续升高。由于塑性变形过程中绝热加热使剪切带中的材料被加热到均匀变形温度区间,强化了变形过程中自由体积的湮灭,导致低温轧制样品中的自由体积含量高于室温轧制样品,并且相同应变量下低温和室温轧制样品之间自由体积含量的差别也随应变速率的增加而减小,使不均匀变形过程中自由体积演化呈现与已有理论完全不一致的变化。
Cu_(60)Zr_(20)Ti_(20)块体非晶合金在轧制变形过程中发生相分离或晶化时材料的显微硬度急剧上升。相分离析出的富Cu非晶相的硬度高于原始非晶相,相分离是导致强化的主要原因。在塑性变形过程中形成的纳米晶体含有明显的晶体缺陷,使得其强化作用下降。在变形非晶合金中相分离可能是比晶化更加有效的强化手段。
Amorphous alloys have become one of the most active fields in the research of advanced materials due to their unique mechanical, physical and chemical properties. However, the criterion of glass forming ability (GFA) of alloys is a critical issue that has not been unsolved yet, and exceptional cases always exist for the known criterions. Traditional quenched amorphous alloys possess very small sizes in at least one dimension, and the obtained strain during deformation at room temperature (RT) is quite limited. The discovery of bulk amorphous alloys (BMA) makes it possible to achieve severe plastic deformation at RT, and provides an opportunity to investigate the microstructural change with changing strains and its influence on various properties of amorphous alloys.
In this dissertation, based on thermodynamics and kinetics of glass-forming process, the essence of GFA of alloys is revisited. By using X-ray diffractometry (XRD), differential scanning calorimetry (DSC) and high resolution transmission electron microscopy (HRTEM), the crystallization mechanism during the isothermal and isochronal annealing of the Cu_(60)Zr_(20)Ti_(20) BMA, the evolution of microstructure and free volume during severe plastic deformation of Cu_(60)Zr_(20)Ti_(20) and Cu_(47.5)Zr_(47.5)Al_5 BMAs are systematically investigated. The microhardness of as-rolled specimens with different amounts of deformation is measured. The present work reveals the evolutions of microstructure, free volume and mechanical property of amorphous alloys with deformation temperature, strain rate and strain during plastic deformation. It provides a new approach to designing the compositions of BMGs and developing amorphous matrix composites.
On the basis of the preconditions of the thermodynamics and kinetics of glass forming, a new criterion evaluating the GFA is proposed, i.e. T_k /T_l ( T_k - Kauzmann temperature, T_l - liquidus temperature of an alloy), and D (fragile parameter of alloy liquid). It is found that T_k /T_l can reflect the GFA well for either the alloys with strong liquid behavior or the alloys with fragile liquid behavior. The larger the T_k /T_l , the better the GFA, and the change in D does not change the role of T_k /T_l . Meanwhile, when the GFAs of these two different alloys are compared, and if T_k /T_l is kept to be the same, the larger the D , the higher the GFA.
The crystallization of Cu_(60)Zr_(20)Ti_(20) BMA proceeds through two reactions. The first is a primary crystallization with precipitation of nano-sized Cu_(51)Zr_(14), and the second is a eutectic one with simultaneous formation of Cu_(51)Zr_(14) and Cu_2ZrTi. Time-dependent nucleation process exists in both crystallization reactions of Cu_(60)Zr_(20)Ti_(20) BMA. The nucleation activation energy of primay Cu_(51)Zr_(14) phase during isothermally annealing the Cu_(60)Zr_(20)Ti_(20) BMA in the supercooled liquid region is not only dependent on the heating rate before isothermal annealing, but also correlated with the definition of incubation time. A higher heating rate leads to a smaller value of nucleation activation energy. However, the effective activation energy for crystallization is not related to the heating rate or the definition of incubation time.
The strain as high as 97% has been achieved during rolling the Cu_(60)Zr_(20)Ti_(20) BMA at both RT and cryogenic temperature (CT, about 150 K), and the as-rolled specimens with large strains remain ductile. Corresponding to each deformation condition, there is a critical strain, below which only shear bands form in the as-rolled specimens, and above which phase transformation occurs. When the rolling temperature or strain rate is increased, the critical strain for occurrence of phase transformation decreases. Meanwhile, the type of phase transformation varies from phase separation to phase separation plus nanocrystallization, and the deviation of the average chemical composition of phase-separated amorphous phases from that of the original alloy is enhanced. When the Cu_(60)Zr_(20)Ti_(20) BMA is rolled at CT at the strain rateε& = 1.0×10~(-4) s~(-1), the specimen remains in a monolithic amorphous state up to the highest strain of 97%. Atε& = 5.0×10-4 s-1, phase separation occurs when the strainεexceeds 93%. With further increasingε& to 5.0×10~(-3) s~(-1), the critical strain for the occurrence of phase separation drops to 89%. At the higherε& of 5.0×10~(-1) s~(-1), phase separation plus nanocrystallization occur atε> 67%. At a givenε& of 5.0×10~(-3) s~(-1), and with increasing the rolling temperature to RT, phase separation plus nanocrystallization also occur atε> 87%. The thermal stability of as-rolled specimens does not obviously change as compared with the as-cast specimen when only shear bands form in the as-rolled and no phase transformation occurs. As phase separation occurs, the thermal stability and crystallization activation energy decrease. If phase separation and nanocrystallization simultaneously take place, the thermal stability and crystallization activation energy will be further reduced.
The saturation of the free-volume content in the monolithic metallic glass without phase transformation at high strains are observed in the Cu_(60)Zr_(20)Ti_(20) BMA during CT-rolling at low strain rates. With increasingε& , the increase rate of the free-volume content in the initial stage of deformation, the critical εabove which the free-volume content in the monolithic metallic glass begins to saturate and the saturated amount of the free-volume content increases. Although the criticalεfor the saturation of the free-volume content in the monolithic metallic glass rises with the strain rate, the criticalεfor phase transformation tends to decrease. The competition of these two critical strains determines whether the saturation of the free-volume content can be obtained when the specimen is still in the monolithic amorphous phase. It is revealed that formation of nano-voids in shear bands through the coalescence of free volume leads to the saturation of free volume. The occurrence of phase separation does not considerably change the free-volume content, while partial nanocrystallization decreases it.
Neither phase separation nor crystallization is induced when the Cu_(47.5)Zr_(47.5)Al_5 BMA is rolled at RT and CT withε& = 5.0×10~(-2) and 5.0×10~(-3) s~(-1), and only compositional and structural heterogeneity in atomic level exists in the amorphous matrix near the shear bands. The free-volume content continuously increases with increasing strain during the whole rolling process. Since the material in the shear bands is adiabatically heated up to the temperature region of homogeneous flow during plastic deformation, enhancing the annihilation of free volume, results in the fact that more free volume is stored in the CT-rolled specimen as compared with the RT-rolled specimen with the same strain, and the difference in the free-volume content between the CT-rolled and RT-rolled specimens with the same strain decreases with the strain rate. The free-volume evolution with temperature and strain rate during the inhomogeneous deformation is totally different from that predicted by the free volume theory.
During rolling the Cu_(60)Zr_(20)Ti_(20) BMA, microhardness dramatically increases when phase separation or phase separation plus nanocrystallization occurs. Since Cu-rich separated amorphous phases from the matrix possess higher strengths than the original amorphous phase, phase separation is the main reason for strengthening. As the deformation-induced nanocrystallites contain lots of crystal defects, their resistance to yielding is deteriorated. In the deformed amorphous alloy, phase separation may be a more effective way to strengthen amorphous alloys than crystallization.
在综合考虑非晶形成热力学和动力学的前提下,提出表征玻璃形成能力的新判据,即T_k /T_l ( T_k -Kauzmann温度, T_l -合金液相线温度)和D(合金液体的脆性参数)。研究发现单独在强液体特性的合金或脆液体特性的合金中, T_k /T_l可以很好地表征合金的玻璃形成能力, T_k /T_l越大,玻璃形成能力越好,并且D值的改变并不影响T_k /T_l的表征作用。同时,在对这两类合金的玻璃形成能力进行比较时,发现当T_k /T_l相等时,D值越大,玻璃形成能力越高。
Cu_(60)Zr_(20)Ti_(20)块体非晶合金的晶化过程为两阶段晶化,第一个晶化反应为初生型晶化,析出纳米尺寸的Cu_(51)Zr_(14)相,第二个晶化反应为共晶型反应,析出晶化相为Cu_(51)Zr_(14)和Cu2ZrTi。时间关联形核过程存在于Cu_(60)Zr_(20)Ti_(20)非晶合金的初生晶化和剩余非晶的晶化过程中。Cu_(60)Zr_(20)Ti_(20)非晶合金在过冷液相区等温晶化时初生Cu_(51)Zr_(14)相的形核激活能不仅与等温退火前的加热速度有关,加热速度越快,形核激活能越小,而且还与孕育期起始点算法有关。但是有效晶化激活能与加热速度和孕育期起始点算法无关。
Cu_(60)Zr_(20)Ti_(20)块体非晶合金在室温和150 K低温轧制过程中获得的最大应变量均高达97%,且大变形后的样品仍具有很好的韧性。对应于每一种变形工艺都存在着一个临界应变量,低于这个临界应变量,样品中只有剪切带产生,高于这个应变量,则有相变发生。无论是提高轧制温度还是提高应变速率,发生相变的临界应变量都下降。相变类型都从单纯的相分离向同时发生相分离和纳米晶化的方向转变,并且相分离后的非晶成分更加偏离合金原始成分。Cu_(60)Zr_(20)Ti_(20)块体非晶合金在150 K低温进行轧制时,如果应变速率ε&= 1.0×10~(-4) s~(-1),试样在轧制到最大应变量97%时仍保持单一非晶状态。当ε& = 5.0×10~(-4) s~(-1)时,试样在应变量ε大于93%时发生相分离。提高ε&至5.0×10~(-3) s~(-1)时,发生相分离的临界应变量降低到89%。在更大的应变速率5.0×10~(-1) s~(-1)下,在ε> 67%时就同时发生相分离和纳米晶化。固定应变速率ε&= 5.0×10~(-3) s~(-1),提高轧制温度到室温,试样在ε> 87%也同时发生相分离和晶化。轧制后的试样只有剪切带而没有相变发生时,非晶合金的热稳定性没有明显变化。相分离一旦出现则会降低非晶合金的热稳定性和退火时的晶化激活能。如果相分离和晶化同时发生,合金的热稳定性和晶化激活能会进一步降低。
在Cu_(60)Zr_(20)Ti_(20)块体非晶合金低温、低应变速率的轧制过程中观察到了单一非晶状态下自由体积在高应变量下的饱和现象。提高应变速率,自由体积在变形初期的增加速度、单一非晶合金试样中自由体积达到饱和的临界应变量以及饱和自由体积含量也随之上升。虽然自由体积饱和的临界应变量随应变速率的上升而上升,但是相变发生的临界应变量却随之下降,这两个临界应变量之间的竞争决定了塑性变形过程中自由体积含量能否在样品还是单一非晶相时达到饱和。剪切带中自由体积崩溃成纳米空洞是导致自由体积饱和的根本原因。相分离的出现并不明显改变自由体积含量,但是晶化的发生使自由体积含量降低。
应变速率为5.0×10~(-3) s~(-1)的298 K室温和150 K低温轧制变形都没有导致Cu_(47.5)Zr_(47.5)Al_5非晶样品发生相分离或晶化,只是在靠近剪切带的非晶基体上,出现了原子尺度的成分结构不均匀性。应变量在从0到最大值97%的变化过程中,自由体积含量持续升高。由于塑性变形过程中绝热加热使剪切带中的材料被加热到均匀变形温度区间,强化了变形过程中自由体积的湮灭,导致低温轧制样品中的自由体积含量高于室温轧制样品,并且相同应变量下低温和室温轧制样品之间自由体积含量的差别也随应变速率的增加而减小,使不均匀变形过程中自由体积演化呈现与已有理论完全不一致的变化。
Cu_(60)Zr_(20)Ti_(20)块体非晶合金在轧制变形过程中发生相分离或晶化时材料的显微硬度急剧上升。相分离析出的富Cu非晶相的硬度高于原始非晶相,相分离是导致强化的主要原因。在塑性变形过程中形成的纳米晶体含有明显的晶体缺陷,使得其强化作用下降。在变形非晶合金中相分离可能是比晶化更加有效的强化手段。
Amorphous alloys have become one of the most active fields in the research of advanced materials due to their unique mechanical, physical and chemical properties. However, the criterion of glass forming ability (GFA) of alloys is a critical issue that has not been unsolved yet, and exceptional cases always exist for the known criterions. Traditional quenched amorphous alloys possess very small sizes in at least one dimension, and the obtained strain during deformation at room temperature (RT) is quite limited. The discovery of bulk amorphous alloys (BMA) makes it possible to achieve severe plastic deformation at RT, and provides an opportunity to investigate the microstructural change with changing strains and its influence on various properties of amorphous alloys.
In this dissertation, based on thermodynamics and kinetics of glass-forming process, the essence of GFA of alloys is revisited. By using X-ray diffractometry (XRD), differential scanning calorimetry (DSC) and high resolution transmission electron microscopy (HRTEM), the crystallization mechanism during the isothermal and isochronal annealing of the Cu_(60)Zr_(20)Ti_(20) BMA, the evolution of microstructure and free volume during severe plastic deformation of Cu_(60)Zr_(20)Ti_(20) and Cu_(47.5)Zr_(47.5)Al_5 BMAs are systematically investigated. The microhardness of as-rolled specimens with different amounts of deformation is measured. The present work reveals the evolutions of microstructure, free volume and mechanical property of amorphous alloys with deformation temperature, strain rate and strain during plastic deformation. It provides a new approach to designing the compositions of BMGs and developing amorphous matrix composites.
On the basis of the preconditions of the thermodynamics and kinetics of glass forming, a new criterion evaluating the GFA is proposed, i.e. T_k /T_l ( T_k - Kauzmann temperature, T_l - liquidus temperature of an alloy), and D (fragile parameter of alloy liquid). It is found that T_k /T_l can reflect the GFA well for either the alloys with strong liquid behavior or the alloys with fragile liquid behavior. The larger the T_k /T_l , the better the GFA, and the change in D does not change the role of T_k /T_l . Meanwhile, when the GFAs of these two different alloys are compared, and if T_k /T_l is kept to be the same, the larger the D , the higher the GFA.
The crystallization of Cu_(60)Zr_(20)Ti_(20) BMA proceeds through two reactions. The first is a primary crystallization with precipitation of nano-sized Cu_(51)Zr_(14), and the second is a eutectic one with simultaneous formation of Cu_(51)Zr_(14) and Cu_2ZrTi. Time-dependent nucleation process exists in both crystallization reactions of Cu_(60)Zr_(20)Ti_(20) BMA. The nucleation activation energy of primay Cu_(51)Zr_(14) phase during isothermally annealing the Cu_(60)Zr_(20)Ti_(20) BMA in the supercooled liquid region is not only dependent on the heating rate before isothermal annealing, but also correlated with the definition of incubation time. A higher heating rate leads to a smaller value of nucleation activation energy. However, the effective activation energy for crystallization is not related to the heating rate or the definition of incubation time.
The strain as high as 97% has been achieved during rolling the Cu_(60)Zr_(20)Ti_(20) BMA at both RT and cryogenic temperature (CT, about 150 K), and the as-rolled specimens with large strains remain ductile. Corresponding to each deformation condition, there is a critical strain, below which only shear bands form in the as-rolled specimens, and above which phase transformation occurs. When the rolling temperature or strain rate is increased, the critical strain for occurrence of phase transformation decreases. Meanwhile, the type of phase transformation varies from phase separation to phase separation plus nanocrystallization, and the deviation of the average chemical composition of phase-separated amorphous phases from that of the original alloy is enhanced. When the Cu_(60)Zr_(20)Ti_(20) BMA is rolled at CT at the strain rateε& = 1.0×10~(-4) s~(-1), the specimen remains in a monolithic amorphous state up to the highest strain of 97%. Atε& = 5.0×10-4 s-1, phase separation occurs when the strainεexceeds 93%. With further increasingε& to 5.0×10~(-3) s~(-1), the critical strain for the occurrence of phase separation drops to 89%. At the higherε& of 5.0×10~(-1) s~(-1), phase separation plus nanocrystallization occur atε> 67%. At a givenε& of 5.0×10~(-3) s~(-1), and with increasing the rolling temperature to RT, phase separation plus nanocrystallization also occur atε> 87%. The thermal stability of as-rolled specimens does not obviously change as compared with the as-cast specimen when only shear bands form in the as-rolled and no phase transformation occurs. As phase separation occurs, the thermal stability and crystallization activation energy decrease. If phase separation and nanocrystallization simultaneously take place, the thermal stability and crystallization activation energy will be further reduced.
The saturation of the free-volume content in the monolithic metallic glass without phase transformation at high strains are observed in the Cu_(60)Zr_(20)Ti_(20) BMA during CT-rolling at low strain rates. With increasingε& , the increase rate of the free-volume content in the initial stage of deformation, the critical εabove which the free-volume content in the monolithic metallic glass begins to saturate and the saturated amount of the free-volume content increases. Although the criticalεfor the saturation of the free-volume content in the monolithic metallic glass rises with the strain rate, the criticalεfor phase transformation tends to decrease. The competition of these two critical strains determines whether the saturation of the free-volume content can be obtained when the specimen is still in the monolithic amorphous phase. It is revealed that formation of nano-voids in shear bands through the coalescence of free volume leads to the saturation of free volume. The occurrence of phase separation does not considerably change the free-volume content, while partial nanocrystallization decreases it.
Neither phase separation nor crystallization is induced when the Cu_(47.5)Zr_(47.5)Al_5 BMA is rolled at RT and CT withε& = 5.0×10~(-2) and 5.0×10~(-3) s~(-1), and only compositional and structural heterogeneity in atomic level exists in the amorphous matrix near the shear bands. The free-volume content continuously increases with increasing strain during the whole rolling process. Since the material in the shear bands is adiabatically heated up to the temperature region of homogeneous flow during plastic deformation, enhancing the annihilation of free volume, results in the fact that more free volume is stored in the CT-rolled specimen as compared with the RT-rolled specimen with the same strain, and the difference in the free-volume content between the CT-rolled and RT-rolled specimens with the same strain decreases with the strain rate. The free-volume evolution with temperature and strain rate during the inhomogeneous deformation is totally different from that predicted by the free volume theory.
During rolling the Cu_(60)Zr_(20)Ti_(20) BMA, microhardness dramatically increases when phase separation or phase separation plus nanocrystallization occurs. Since Cu-rich separated amorphous phases from the matrix possess higher strengths than the original amorphous phase, phase separation is the main reason for strengthening. As the deformation-induced nanocrystallites contain lots of crystal defects, their resistance to yielding is deteriorated. In the deformed amorphous alloy, phase separation may be a more effective way to strengthen amorphous alloys than crystallization.
引文
[1] 郑兆勃,非晶固态材料引论,科学出版社,1987.
[2] 程天一,章守华,快速凝固技术与新型合金,宇航出版社,1990.
[3] M. Telford, The case for bulk metallic glass, Materials Today, 2004, 3: 36-43.
[4] W. Klement, R. Willens, P. Duwez, Non-crystalline structure in solidified gold-silicon alloys, Nature, 1960, 187: 869-870.
[5] S. Kavesh, in: Metallic Glass, J.J. Gillman, H.L. Leamy (Eds.), ASM International, Metals Park, OH, 1978.
[6] H.S. Chen, Thermodynamic considerations on the formation and stability of metallic glasses, Acta Metall., 1974, 22: 1505-1511.
[7] A.J. Drenhman, A.L. Greer, D. Turnbull, Bulk formation of a metallic glass: Pd_(40)Ni_(40)P_(20), Appl. Phys. Lett., 1982, 41: 716-717.
[8] H.W. Kui, A.L. Greer, D. Turnbull, Formation of bulk metallic glass by fluxing, Appl. Phys. Lett., 1984, 45: 615-616.
[9] H.W. Kui, D. Turnbull, Melting of Ni_(40)Pd_(40)P_(20) glass, Appl. Phys. Lett., 1985, 47: 796-798.
[10] A. Inoue, T. Zhang, T. Masumoto, Al-La-Ni amorphous alloys with a wide supercooled liquid region, Mater. Trans. JIM, 1989, 30: 965-972.
[11] A. Inoue, T. Masumoto, Mg-based amorphous alloys, Mater. Sci. Eng. A, 1993, 173:1-8.
[12] A. Inoue, T. Zhang, T. Masumoto, Zr-Al-Ni amorphous alloys with high glass transition temperature and significant supercooled liquid region, Mater. Trans. JIM, 1990, 31: 177-183.
[13] A. Inoue, T. Zhang, Fabrication of bulk glassy Zr_(55_Al_(10)Ni_5Cu_(30) alloy of 30 mm in diameter by a suction casting method, Mater. Trans. JIM, 1996, 37: 185-187.
[14] A. Inoue, J.S. Gook, Multicomponent Fe-based glassy alloys with wide supercooled liquid region before crystallization, Mater. Trans. JIM, 1995, 36: 1282-1285.
[15] A. Inoue, T. Zhang, A. Takeuchi, Bulk amorphous alloys with high mechanical strength and good soft magnetic properties in Fe-TM-B (TM=IV-VIII group transiton metal) system, Appl. Phys. Lett., 1997, 71: 464-466.
[16] A. Inoue, N. Nishiyama, T. Matsudu, Preparation of bulk glassy Pd_(40)Ni_(10)Cu_(20)P_(30) alloy of 40 mm in diameter by water quenching, Mater. Trans. JIM, 1996, 37: 181-184.
[17] A. Inoue, N. Nishiyama, H.M. Kimura, Preparation and thermal stability of bulk amorphous Pd_(40)Cu_(20)Ni_(10)P_(30) alloy of 72 mm in diameter, Mater. Trans. JIM, 1997, 38: 179-183.
[18] A. Inoue, N. Nishiyama, K. Amiya, T. Zhang, T. Masumoto, Ti-based amorphous alloys with a wide supercooled liquid region, Mater. Lett., 1994, 19: 131-135.
[19] X. Wang, I. Yoshii, A. Inoue, Y.H. Kim, I.B. Kim, Bulk amorphous Ni_(75-x)Nb_5M_xP_(20-y)B_y (M= Cr, Mo) alloy with large supercooling and high strength, Mater. Trans. JIM, 1999, 40: 1130-1136.
[20] T. Zhang, A. Inoue, New bulk glassy Ni-based alloys with high strength of 3000 Mpa, Mater. Trans. JIM, 2002, 43: 708-711.
[21] A. Inoue, A. Katsuya, Multicomponent Co-based amorphous alloys with wide supercooled liquid region, Mater. Trans. JIM, 1996, 37: 1332-1336.
[22] A. Inoue, W. Zhang, T. Zhang, K. Kurosaka, High-strength Cu-based bulk glassy alloys in Cu-Zr-Ti and Cu-Hf-Ti ternary system, Acta Mater., 2001, 49: 2645-2652.
[23] A. Peker, W.L. Johnson, A highly processable metallic glass: Zr_(41.2)Ti_(13.8)Cu_(12.5)Ni_(10)Be_(22.5), Appl. Phys. Lett., 1993, 63: 2342-2344.
[24] C.C. Koch, O.B. Cavin, C.G. McKamey, J.O. Scarbrough, Preparation of “amorphous” Ni_(60)Nb_(40) by mechanical alloying, Appl. Phys. Lett., 1983, 43: 1017-1019.
[25] A. Biswas, G.K. Dey, A.J. Haq, D.K. Bose, S. Banerjee, A study of solid-state amorphization in Zr-30at.% Al by mechanical attrition, J. Mater. Res., 1996, 11: 599-607.
[26] C. Suryanaraya, Mechanical alloying and milling, Prog. Mater. Sci., 2001, 46: 1-148.
[27] A. Inoue, Stabilization of metallic supercooled liquid and bulk amorphous alloys, Acta Mater., 2000, 48: 279-306.
[28] A. Inoue, B.L. Shen, C.T. Chang, Super-high strength of over 4000 MPa for Fe-based bulk glassy alloys in FeCoBSiNb system, Acta Mater., 2004, 52: 4093-4099.
[29] A. Inoue, B.L. Shen, H. Koshiba, H. Kato, A.R. Yavari, Ultra-high strength above 5000 MPa and soft magnetic properties of Co-Fe-Ta-B bulk glassy alloys, Acta Mater., 2004, 52: 1631-1637.
[30] W.L. Johnson, Fundamental aspects of bulk metallic glass formation in multicomponent alloys, Mater. Sci. Forum, 1996, 225-227: 35-49.
[31] H. Bei, S. Xie, E.P. George, Softening caused by profuse shear banding in a bulk metallic glass, Phys. Rev. Lett., 2006, 96: 105503.
[32] H.J. Leamy, H.S. Chen, T.T. Wang, Plastic flow and fracture of metallic glass, Metall. Trans., 1972, 3: 699-708.
[33] A. Inoue, Y. Kawamura, Y. Saotome, High strain rate superplasticity of supercooled liquid for amorphous alloys, Mater. Sci. Forum, 1997, 233-234: 147-154.
[34] Kawamura Y., Shibata T., Inoue A., Masumoto T., Workability of the supercooled liquid in the Zr_(65)Al_(10)Ni_(10)Cu_(15) bulk metallic glass, Acta Mater., 1998, 46: 253-263.
[35] H. Jones, Rapid solidification of metals and alloys, Inst. of Metallurgists, London, 1982.
[36] A. Inoue, T. Zhang, W. Zhang, A. Takeuchi, Bulk Nd-Fe-Al amorphous alloys with hard magnetic properties, Mater. Trans. JIM, 1996, 37: 99-108.
[37] A. Inoue, T. Zhang, A. Takeuchi, W. Zhang, Hard Magnetic Bulk Amorphous Nd-Fe-Al Alloys of 12 mm in Diameter Made by Suction Casting, Mater. Trans. JIM, 1996, 37: 636-640.
[38] A. Inoue, A. Takeuchi, Recent progress in bulk glassy alloys, Mater. Trans. JIM, 2002, 43: 1892-1906.
[39] W.H. Wang, C. Dong, C.H. Shek, Bulk metallic glasses, Mater. Sci. Eng. R., 2004, 44: 45-89.
[40] D.M. Herlach, Non-equilibrium solidification of undercooled metallic melts, Mater. Sci. Eng. R., 1994, 12: 177-272.
[41] C.A. Angell, Formation of glass from liquid and biopolymers, Science, 1995, 267: 1924-1935.
[42] Z.P. Lu, Y. Li, S.C.Ng, Reduced glass transition temperature and glass forming ability of bulk glass forming alloys, J. Non-cryst. Solids, 2000, 270: 103-114.
[43] M.H. Cohen, D. Turnbull, Molecular transport in liquids and glasses, J. Chem. Phys., 1959, 31: 1164-1169.
[44] D. Turnbull, M.H. Cohen, Free-volume model of the amorphous phase: glass transition, J. Chem. Phys., 1961, 34: 120-125.
[45] Z.P. Lu, C.T. Liu, A new glass-forming ability criterion for bulk metallic glass, Acta Mater., 2002, 50: 3501-3512.
[46] M. Ouchetto, B. Elouadi, S. Parke, Study of Lanthanide zinc phosphate glasses by differential thermal analysis, Phys. Chem. Glasses, 1991, 32: 22-28.
[47] A. Inoue, T. Zhang, T. Masumoto, Glass-forming ability of alloys, J. Non-cryst. Solids, 1993, 156-158: 473-480.
[48] T.A. Waniuk, J. Schroers, W.L. Johnson, Critical cooling rate and thermal stability of Zr-Ti-Cu-Ni-Be alloys, Appl. Phys. Lett., 2001, 78: 1213-1215.
[49] Z.P. Lu, C.T. Liu, Glass formation criterion for various glass-forming systems, Phys. Rev. Lett., 2003, 91: 115515.
[50] T. Egami, V. Vitek, D. Srolovitz, in Rapidly Quenched Metals IV, ed. by T. Masumoto, K. Suzuki, Japan Inst. Met., Sendai, 1981.
[51] A. Inoue, Preparation and novel properties of nanocrystalline and nanoquasicrystalline alloys, Nanostruct. Mater., 1995, 6: 53-64.
[52] F. Spaepen, A microscopic mechanism for steady state inhomogeneous flow in metallic glasses, Acta Metall., 1977, 25: 407-415.
[53] D. Turnbull, Under what conditions can a glass be formed?, Contemp. Phys., 1969, 10: 473-488.
[54] M.H. Cohen, G.S. Grest, Liquid-glass transition, a free-volume approach, Phys. Rev. B, 1979, 20: 1077-1098.
[55] P.G. Debenedetti, F.H. Stillinger, Supercooled liquids and the glass transition, Nature, 2001, 410: 259-267.
[56] K.M. Flores, D. Suh, R.H. Dauskardt, P. Asoka-Kumar, P.A. Sterne, R.H. Howell, Characterization of free volume in a bulk metallic glass using positron annihilation spectroscopy, J. Mater. Res., 2002, 17: 1153-1161.
[57] P.S. Steif, F. Spaepen, J.W. Prevost, Strain localization in amorphous metals, Acta Metall., 1982, 30: 447-455.
[58] A.S. Argon, Plastic deformation in metallic glasses, Acta Metall., 1979, 27: 47-58.
[59] R. Huang, Z. Suo, J.H. Prevost, W.D. Nix, Inhomogeneous deformation in metallic glasses, J. Mech. Phys. Solids, 2002, 50: 1011-1027.
[60] W.J. Wright, R.B. Schwarz, W.D. Nix, Localized heating during serrated plastic flow in bulk metallic glasses, Mater. Sci. Eng. A, 2001, 319-321: 229-232.
[61] J.J. Kim, Y. Choi, S. Suresh, A.S. Argon, Nanocrystallization during nanoindentation of a bulk amorphous metal alloy at room temperature, Science, 2002, 295: 654-657.
[62] H.A. Bruck, A.J. Rosakis, W.L. Johnson, The dynamic compressive behavior of beryllium bearing bulk metallic glasses, J. Mater. Res., 1996, 11: 503-511.
[63] K.M. Flores, R.H. Dauskardt, Mean stress effects on flow localization and failure ina bulk metallic glass, Acta Mater., 2001, 49: 2527-2537.
[64] J.J. Lewandowski, A.L. Greer, Temperature rise at shear bands in metallic glasses, Nature Mater., 2006, 5: 15-18.
[65] Q.K. Li, M. Li, Atomic scale characterization of shear bands in an amorphous metal, Appl. Phys. Lett., 2006, 88: 241903.
[66] M.C. Gao, R.E. Hackenberg, G.J. Shiflet, Deformation-induced nanocrystal precipitation in Al-base metallic glasses, Mater. Trans. JIM, 2001, 42: 1741-1747.
[67] Y. He, G.J. Shiflet, S.J. Poon, Ball milling-induced nanocrystal formation in aluminum-based metallic glasses, Acta Metall., 1995, 43: 83-91.
[68] H. Chen, Y. He, G.J. Shiflet, S.J. Poon, Deformation-induced nanocrystal formation in shear bands of amorphous alloys, Nature, 1994, 367: 541-543.
[69] W.H. Jiang, M. Atzmon, The effect of compression and tension on shear-band structure and nanocrystallization in amorphous Al_(90)Fe_5Ga_5: a high-resolution transmission electron microscopy study, Acta Mater., 2003, 51: 4095-4105.
[70] W.H. Jiang, F.E. Pinkerton, M. Atzmon, Deformation-induced nanocrystallization in an Al-based amorphous alloy at subambient temperature, 2003, 48: 1195-1200.
[71] D.V. Louzguine, A. Inoue, Nanocrystallization of Cu-(Zr or Hf)-Ti metallic glasses, J. Mater. Res., 2002, 17: 2112-2120.
[72] M.W. Chen, A. Inoue, W. Zhang, T. Sakurai, Extraordinary plasticity of ductile bulk metallic glasses, Phys. Rev. Lett., 2006, 96: 245502.
[73] R.J. Hebert, J.H. Perepezko, Effect of cold-rolling on the crystallization behavior of amorphous Al_(88)Y_7Fe_5 alloy, Mater. Sci. Eng. A, 2004, 375-377: 728-732.
[74] W.L. Johnson, Thermodynamic and kinetic aspects of the crystal to glass transformation in metallic materials, Prog. Mater. Sci., 1986, 30: 81-134.
[75] A. Inoue, Bulk amorphous alloys-preparation and fundamental characteristics, Trans Tech Publications Ltd., Switzerland, 1998.
[76] H.S. Chen, Stored energy in a cold-rolled metallic glass, Appl. Phys. Lett., 1976, 29:328-330.
[77] J. Das, M.B. Tang, K.B. Kim, R. Theissmann, F. Baier, W.H. Wang, J. Eckert, “Work-hardenable ” ductile bulk metallic glass, Phys. Rev. Lett. 2005, 94: 205501.
[78] D.H. Xu, B. Lohwongwatana, G. Duan, W.L. Johnson, C. Garland, Bulk metallic glass formation in binary Cu-rich alloy series – Cu_(100-x)Zr_x (x = 34, 36, 38.2, 40 at.%) and mechanical properties of bulk Cu_(64)Zr_(36) glass, Acta Mater., 2004, 52: 2621-2624.
[79] G. Duan, D.H. Xu, W.L. Johnson, High copper content bulk glass formation in bimetallic Cu-Hf system, Metall. Mater. Trans. A, 2005, 36: 455-458.
[80] S. Sastry, The relationship between fragility, configurational entropy and the potential energy landscape of glass-forming liquids, Nature, 2001, 409: 164-167.
[81] W.L. Johnson, J. Lu, M.D. Demetriou, Deformation and flow in bulk metallic glasses and deeply undercooled glass forming liquids – a self consistent dynamic free volume model, Intermetallics, 2002, 10: 1039-1046.
[82] W. Kauzmann, The Nature of the glassy state and the behavior of liquids at low temperatures, Chem. Rev., 1948, 43: 219-256.
[83] J. Jackle, Models of the glass transition, Rep. Prog. Phys., 1986, 49: 171-231.
[84] M. Lasocka, The effect of scanning rate on glass transition temperature of splat-cooled Te_(85)Ge_(15), Mater. Sci. Eng., 1976, 23: 173-177.
[85] R. Bruning, K. Samwer, Glass transition on long time scales, Phys. Rev. B, 1992, 46:11318-11322.
[86] T.A. Waniuk, R. Busch, A. Masuhr, W.L. Johnson, Equilibrium viscosity of the Zr_(41.2)Ti_(13.8)Cu_(12.5)Ni_(10)Be_(22.5) bulk metallic glass-forming liquid and viscous flow during relaxation, phase separation, and primary crystallization, Acta Mater., 1998, 46: 5229-5236.
[87] R. Busch, E. Bakke, W.L. Johnson, Viscosity of the supercooled liquid and relaxation at the glass transition of the Zr_(46.75)Ti_(8.25)Cu_(7.5)Ni_(10)Be_(27.5) bulk metallic glass forming alloy, Acta Mater., 1998, 46: 4725-4732.
[88] R. Busch, W. Liu, W.L. Johnson, Thermodynamics and kinetics of the Mg65Cu25Y10 bulk metallic glass forming liquid, J. Appl. Phys., 1998, 83: 4134-4141.
[89] Z.P. Lu, Y. Li, C.T. Liu, Glass-forming tendency of bulk La-Al-Ni-Cu-(Co) metallic glass-forming liquids, J. Appl. Phys., 2003, 93: 286-290.
[90] L. Shadowspeaker, R. Busch, On the fragility of Nb-Ni-based and Zr-based bulk metallic glasses, Appl. Phys. Lett., 2004, 85: 2508-2510.
[91] R. Busch, A. Masuhr, W.L. Johnson, Thermodynamics and kinetics of Zr–Ti–Cu–Ni-Be bulk metallic glass forming liquids, Mater. Sci. Eng. A, 2001, 304-306: 97-102.
[92] S.C. Glade, W.L. Johnson, Viscous flow of the Cu_(47)Ti_(34)Zr_(11)Ni_8 glass forming alloy, J. Appl. Phys., 2000, 87: 7249-7251.
[93] G. Wilde, G.P. Gorler, R. Willnecker, H.J. Frecht, Calorimetric, thermomechanical, and rheological characterizations of bulk glass-forming Pd_(40)Ni_(40)P_(20), J. Appl. Phys., 2000, 87:1141-1152.
[94] K. Kawamura, A. Inoue, Newtonian viscosity of supercooled liquid in a Pd_(40)Ni_(40)P_(20) metallic glass, Appl. Phys. Lett., 2000, 77: 1114-1116.
[95] N. Nishiyama, A. Inoue, Flux treated Pd-Cu-Ni-P amorphous alloy having low critical cooling rate, Mater. Trans. JIM, 1997, 38: 464-472.
[96] R. Elliott, in: Eutectic solidification processing, crystalline and glassy alloy. Bodmin, (Cornwall): Robert Hartnoll; 1983. p.38.
[97] X.H. Lin, W.L. Johnson, Formation of Ti-Zr-Cu-Ni bulk metallic glasses, J. Appl. Phys., 1995, 78: 6514-6519.
[98] T. Zhang, A. Inoue, Preparation of Ti-Cu-Ni-Si-B amorphous alloys with a large supercooled liquid region, Mater. Trans., JIM, 1999, 40: 301.
[99] C. Li, J. Saida, M. Kiminami, A. Inoue, Dynamic crystallization process in a supercooled liquid region of Cu_(40)Ti_(30)Ni_(15)Zr_(10)Sn_5 amorphous alloy, J Non-Cryst Solids, 2000, 261: 108-114.
[100] A. Inoue, W. Zhang, T. Zhang,, K. Kurosaka, Thermal and mechanical properties of Cu-based Cu-Zr-Ti bulk glassy alloys, Mater. Trans. 2001, 42: 1149-1151.
[101] A. Inoue, W. Zhang, T. Zhang, K. Kurosaka, Formation and mechanical properties of Cu-Hf-Ti bulk glassy alloys, J. Mater. Res. 2001, 16: 2836-2844.
[102] A. Inoue, W. Zhang, T. Zhang, K. Kurosaka, Cu-based bulk glassy alloys with good mechanical properties in Cu-Zr-Hf-Ti system, Mater. Trans. 2001, 42: 1805-1812.
[103] J.Z. Jiang, H. Kato, T. Ohsuna, J. Saida, A. Inoue, K. Saksl, H. Franz, K. Stahl, Origin of nondetectable x-ray diffraction peaks in nanocomposite CuTiZr alloys, Appl. Phys. Lett., 2003, 83: 3299-3301.
[104] J.Z. Jiang, B. Yang, K. Saksl, H. Franz, N. Pryds, Crystallization of Cu_(60)Ti_(20)Zr_(20) metallic glass with and without pressure, J. Mater. Res., 2003, 18: 895-898.
[105] A. Concustell, A. Revesz, S. Surinach, M.D. Baro, L.K. Varga, G. Heunen, Microstructural evolution during decomposition and crystallization of the Cu_(60)Zr_(20)Ti_(20) amorphous alloy, J. Mater. Res., 2004, 19: 505-512.
[106] W.A. Johnson, R.F. Mehl, Reaction kinetics in processes of nucleation and growth, Trans. Am. Inst. Min. Metall. Pet. Eng., 1939, 135: 416-458.
[107] M. Avrami, Granulation, phase change and microstructure. Kinetics of phase change. III., J. Chem. Phys., 1941, 9: 177-184.
[108] J.W. Christian, The theory of transformation in metals and alloys, Pergamon Press, Oxford, 2002.
[109] 徐祖耀,相变原理,科学出版社,2000.
[110] J.Z. Jiang, Y.X. Zhuang, H. Rasmussen, J. Saida, A. Inoue, Formation of quasicrystals and amorphous-to-quasicrystalline phase transformation kinetics in Zr_(65)Al_(7.5)Ni_(10)Cu_(7.5)Ag_(10) metallic glass under pressure, Phys. Rev. B, 2001, 64: 094208.
[111] J.B. Zeldovich, On the theory of new phase formation; cavitation., Acta Physicochim URSS, 1943, 18: 1-22.
[112] D. Kashchiev, Solution of non-steady problem in nucleation kinetics, Surf. Sci., 1969, 14: 209-214.
[113] K. Lu, X.D. Liu, F.H. Yuan, Synthesis of the NiZr_2 intermetallic compound nanophase materials, Physica B, 1996, 217: 153-159.
[114] K.F. Kelton, Crystal Nucleation in Liquids and Glasses, Solid State Phys., 1991, 45: 75-178.
[115] D. Turnbull, in: Physics of non-crystalline solids, J.A. Prins (Ed.), North-Holland, Amsterdam, 1964.
[116] H.S. Chen, S.Y. Chuang, Phys. Stat. Sol. A, 1974, 25: 581.
[117] D. Holland-Moritz, Short-range order and solid-liquid interface in undercooled metallic melts, Mater. Sci. Eng. A, 2001, 304-306: 108-113.
[118] F. Spaepen, Structural model for the solid-liquid interface in monatomic systems, Acta Metall., 1975, 23: 729-743.
[119] F. Spaepen, R.B. Meyer, Surface tension in a structural model for the liquid-liquid interface, Scripta Metall., 1976, 10: 37-43.
[120] F. Ye, K. Lu, Pressure effect on polymorphous crystallization kinetics in amorphous selenium, Acta Mater., 1998, 46: 5965-5971.
[121] F. Zhou, R. Luck, K. Lu, E.J. Lavernia, M. Ruhle, Amorphous-to-crystalline transformation induced by thermal annealing of a metastable Al_(90)Fe_(10) composite, Phil. Mag. A, 2002, 82: 1003-1015.
[122] Y.X. Zhuang, J.Z. Jiang, Z.G. Lin, M. Mezouar, W. Crichton, A. Inoue, Evidence of eutectic crystallization and transient nucleation in Al_(89)La_6Ni_5 amorphous alloy, Appl. Phys. Lett., 2001, 79: 743-745.
[123] R. Arroyave, T.W. Eagar, L. Kaufman, Thermodynamic assessment of the Cu-Ti-Zr system, J. Alloys Comp., 2003, 351: 158-170.
[124] A.R. Miedema, F.J.A. den Broeder, On the interfacial energy in solid-liquid and solid-solid metal combination, Z. Metallkd., 1979, 70: 14-20.
[125] H.E. Kissinger, Variation of peak temperature with heating rate in differential thermal analysis, J. Res. Natl Bur. Stand., 1956, 57: 217-221.
[126] Y.Q. Gao, W. Wang, On the activation energy of crystallization in metallic glasses, J. Non-Cryst. Solids, 1986, 81: 129-134.
[127] A.T.W. Kempen, F. Sommer, E.J. Mittemeijer, Determination and interpretation of isothermal and non-isothermal transformation kinetics: the effective activation energies in terms of nucleation and growth, J. Mater. Sci., 2002, 37: 1321-1332.
[128] A.T.W. Kempen, F. Sommer, E.J. Mittemeijer, The isothermal and isochronal kinetics of the crystallisation of bulk amorphous Pd_(40)Cu_(30)P_(20)Ni_(10), Acta Mater., 2002, 50: 1319-1329.
[129] S. Ranganathan, M. von Heimendahl, Three activation energies with isothermal transformation: Applications to metallic glasses, J. Mater. Sci., 1981, 16: 2401-2404.
[130] Y.X. Zhuang, W.H. Wang, Y. Zhang, M.X. Pan, D.Q. Zhao, Crystallization kinetics and glass transition of Zr_(41)Ti_(14)Cu_(12.5)Ni_(10-x)Fe_xBe_(22.5) bulk metallic glasses, Appl. Phys. Lett., 1999, 75: 2392-2394.
[131] B.G. Bagley, E.M. Vogel, Crystallization kinetics of glassy Pd_(0.775)Cu_(0.06)Si_(0.165), J. Non-Cryst. Solids, 1975, 18: 29-32.
[132] M.V. Susic, P.B. Budberg, S.P. Alisova, Kinetics of thermal devitrification (crystallization) of a titanium amorphous alloy, J. Mater. Sci., 1986, 21: 1297-1300.
[133] L. Liu, Z.F. Wu, L. Chen, A kinetic study of the non-isothermal crystallization of a Zr-based bulk metallic glass, Chin. Phys. Lett., 2002, 19: 1483-1486.
[134] F.R. de Boer, R. Boom, W.C.M. Matterns, A.R. Miedena, A.K. Niessen, Cohesion in Metals, Elsevier Science, Amsterdam, 1989.
[135] W.L. Johnson, Bulk glass-forming metallic alloys: science and technology, MRS Bull., 1999, 24: 42-56.
[136] 周玉、武高辉,材料分析测试技术,哈尔滨工业大学出版社,1998.
[137] B.J. Park, H.J. Chang, D.H. Kim, W.T. Kim, In situ formation of two amorphousphases by liquid phase separation in Y-Ti-Al-Co alloy, Appl Phys Lett 2004;85:6353.
[138] S. Schneider, P. Thiyagarajan, W.L. Johnson, Formation of nanocrystals based on decomposition in the amorphous Zr_(41.2)Ti_(13.8)Cu_(12.5)Ni_(10)Be_(22.5) alloy, Appl. Phys. Lett., 1996, 68: 493-495.
[139] A.A. Kundig, M. Ohnuma, D.H. Ping, T. Ohkubo, K. Hono, In situ formed two-phase metallic glass with surface fractal microstructure, Acta Mater., 2004, 52: 2441-2448.
[140] P. de Hey, J. Sietsma, A. van den Beukel, Structural disordering in amorphous Pd_(40)Ni_(40)P_(20) induced by high temperature deformation, Acta Mater., 1998, 46:5873-5882.
[141] A. van den Beukel, J. Sietsma, Glass transition as a free volume related kinetic phenomenon, Acta Metall., 1990, 38: 383-389.
[142] M. Heggen, F. Spaepen, M. Feuerbacher, Creation and annihilation of free volume during homogeneous flow of a metallic glass, J. Appl. Phys., 2005, 97: 033506.
[143] P.D. Miller, J.M. Gibson, Connecting small-angle diffraction with real-space images by quantitative transmission electron microscopy of amorphous thin-films, Ultramicroscopy, 1998, 74: 221-235.
[144] H.Q. Li, K.X. Tao, C. Fan, P.K. Liaw, H. Choo, Effect of temperature on mechanical behavior of Zr-based bulk metallic glasses, Appl. Phys. Lett., 2006, 89: 041921.
[145] N. Morito, Internal friction study on structure relaxation of a glassy metal Fe_(32)Ni_(36)Cr_(14)P_(12)B_6, Mater. Sci. Eng., 1983, 60: 261-268.
[146] J.D. Eshelby, P.L. Pratt, Note on the heating effect of moving dislocations, Acta Metall., 1956, 4: 560-562.
[147] T. Mukai, T.G. Nieh, Y. Kawamura, A. Inoue, K. Higashi, Dynamic response of a Pd40Ni40P20 bulk metallic glass in tension, Scripta Mater., 2002, 46: 43-47.
[148] W.H. Jiang, M. Atzmon, Mechanical strength of nanocrystalline/amorphous Al_(90)Fe_5Gd_5 composites produced by rolling, Appl. Phys. Lett., 2005, 86: 151916.
[149] H.M. Pollock, D. Maugis, M. Barquins, in: Microindentation Techniques in Materials Science and Engineering, P.J. Blau, B.R. Lawn (Eds.), American Society for Testing and Materials Special Technical Publications 889, Philadelphia, 1986, pp. 47-71.
[150] T. Abe, M. Shimono, K. Hashimoto, K. Hono, H. Onodera, Phase separation and glass-forming abilities of ternary alloys, Scripta Mater., 2006, 55: 421-424.
[151] J.Z. Jiang, W. Roseker, L. Gerward, G. Goerigk, Is there phase separation in Cu_(60)Ti_(20)Zr_(20) alloy?, J. Metastable Nanocrystal Mater., 2005, 24-25: 647-652.
[152] H.S. Kim, S.I. Hong, Model of the ductile-brittle transition of partially crystallized amorphous Al-Ni-Y alloys, Acta Mater., 1999, 47: 2059-2066.
[153] N. Chen, D.V. Louzguine, S. Ranganathan, A. Inoue, Formation ranges of icosahedral, amorphous and crystalline phases in rapidly solidified Ti-Zr-Hf-Ni alloys, Acta Mater., 2005, 53: 759-764.
[154] C. Fan, A. Inoue, Ductility of bulk nanocrystalline composites and metallic glasses at room temperature, Appl. Phys. Lett., 2000, 77: 46-48.
[155] C.C. Hays, C.P. Kim, W.L. Johnson, Microstructure controlled shear band pattern formation and enhanced plasticity of bulk metallic glasses containing in situ formed ductile phase dendrite dispersions, Phys. Rev. Lett., 2000, 84: 2901-2904.
[156] U. Kuhn, J. Eckert, N. Mattern, L. Schultz, ZrNbCuNiAl bulk metallic glass matrix composites containing dendritic bcc phase precipitates, Appl. Phys. Lett., 2002, 80: 2478-2480.
[157] H. Choi-Yim, W.L. Johnson, Bulk metallic glass matrix composites, Appl. Phys. Lett., 1997, 71: 3808-3810.
[2] 程天一,章守华,快速凝固技术与新型合金,宇航出版社,1990.
[3] M. Telford, The case for bulk metallic glass, Materials Today, 2004, 3: 36-43.
[4] W. Klement, R. Willens, P. Duwez, Non-crystalline structure in solidified gold-silicon alloys, Nature, 1960, 187: 869-870.
[5] S. Kavesh, in: Metallic Glass, J.J. Gillman, H.L. Leamy (Eds.), ASM International, Metals Park, OH, 1978.
[6] H.S. Chen, Thermodynamic considerations on the formation and stability of metallic glasses, Acta Metall., 1974, 22: 1505-1511.
[7] A.J. Drenhman, A.L. Greer, D. Turnbull, Bulk formation of a metallic glass: Pd_(40)Ni_(40)P_(20), Appl. Phys. Lett., 1982, 41: 716-717.
[8] H.W. Kui, A.L. Greer, D. Turnbull, Formation of bulk metallic glass by fluxing, Appl. Phys. Lett., 1984, 45: 615-616.
[9] H.W. Kui, D. Turnbull, Melting of Ni_(40)Pd_(40)P_(20) glass, Appl. Phys. Lett., 1985, 47: 796-798.
[10] A. Inoue, T. Zhang, T. Masumoto, Al-La-Ni amorphous alloys with a wide supercooled liquid region, Mater. Trans. JIM, 1989, 30: 965-972.
[11] A. Inoue, T. Masumoto, Mg-based amorphous alloys, Mater. Sci. Eng. A, 1993, 173:1-8.
[12] A. Inoue, T. Zhang, T. Masumoto, Zr-Al-Ni amorphous alloys with high glass transition temperature and significant supercooled liquid region, Mater. Trans. JIM, 1990, 31: 177-183.
[13] A. Inoue, T. Zhang, Fabrication of bulk glassy Zr_(55_Al_(10)Ni_5Cu_(30) alloy of 30 mm in diameter by a suction casting method, Mater. Trans. JIM, 1996, 37: 185-187.
[14] A. Inoue, J.S. Gook, Multicomponent Fe-based glassy alloys with wide supercooled liquid region before crystallization, Mater. Trans. JIM, 1995, 36: 1282-1285.
[15] A. Inoue, T. Zhang, A. Takeuchi, Bulk amorphous alloys with high mechanical strength and good soft magnetic properties in Fe-TM-B (TM=IV-VIII group transiton metal) system, Appl. Phys. Lett., 1997, 71: 464-466.
[16] A. Inoue, N. Nishiyama, T. Matsudu, Preparation of bulk glassy Pd_(40)Ni_(10)Cu_(20)P_(30) alloy of 40 mm in diameter by water quenching, Mater. Trans. JIM, 1996, 37: 181-184.
[17] A. Inoue, N. Nishiyama, H.M. Kimura, Preparation and thermal stability of bulk amorphous Pd_(40)Cu_(20)Ni_(10)P_(30) alloy of 72 mm in diameter, Mater. Trans. JIM, 1997, 38: 179-183.
[18] A. Inoue, N. Nishiyama, K. Amiya, T. Zhang, T. Masumoto, Ti-based amorphous alloys with a wide supercooled liquid region, Mater. Lett., 1994, 19: 131-135.
[19] X. Wang, I. Yoshii, A. Inoue, Y.H. Kim, I.B. Kim, Bulk amorphous Ni_(75-x)Nb_5M_xP_(20-y)B_y (M= Cr, Mo) alloy with large supercooling and high strength, Mater. Trans. JIM, 1999, 40: 1130-1136.
[20] T. Zhang, A. Inoue, New bulk glassy Ni-based alloys with high strength of 3000 Mpa, Mater. Trans. JIM, 2002, 43: 708-711.
[21] A. Inoue, A. Katsuya, Multicomponent Co-based amorphous alloys with wide supercooled liquid region, Mater. Trans. JIM, 1996, 37: 1332-1336.
[22] A. Inoue, W. Zhang, T. Zhang, K. Kurosaka, High-strength Cu-based bulk glassy alloys in Cu-Zr-Ti and Cu-Hf-Ti ternary system, Acta Mater., 2001, 49: 2645-2652.
[23] A. Peker, W.L. Johnson, A highly processable metallic glass: Zr_(41.2)Ti_(13.8)Cu_(12.5)Ni_(10)Be_(22.5), Appl. Phys. Lett., 1993, 63: 2342-2344.
[24] C.C. Koch, O.B. Cavin, C.G. McKamey, J.O. Scarbrough, Preparation of “amorphous” Ni_(60)Nb_(40) by mechanical alloying, Appl. Phys. Lett., 1983, 43: 1017-1019.
[25] A. Biswas, G.K. Dey, A.J. Haq, D.K. Bose, S. Banerjee, A study of solid-state amorphization in Zr-30at.% Al by mechanical attrition, J. Mater. Res., 1996, 11: 599-607.
[26] C. Suryanaraya, Mechanical alloying and milling, Prog. Mater. Sci., 2001, 46: 1-148.
[27] A. Inoue, Stabilization of metallic supercooled liquid and bulk amorphous alloys, Acta Mater., 2000, 48: 279-306.
[28] A. Inoue, B.L. Shen, C.T. Chang, Super-high strength of over 4000 MPa for Fe-based bulk glassy alloys in FeCoBSiNb system, Acta Mater., 2004, 52: 4093-4099.
[29] A. Inoue, B.L. Shen, H. Koshiba, H. Kato, A.R. Yavari, Ultra-high strength above 5000 MPa and soft magnetic properties of Co-Fe-Ta-B bulk glassy alloys, Acta Mater., 2004, 52: 1631-1637.
[30] W.L. Johnson, Fundamental aspects of bulk metallic glass formation in multicomponent alloys, Mater. Sci. Forum, 1996, 225-227: 35-49.
[31] H. Bei, S. Xie, E.P. George, Softening caused by profuse shear banding in a bulk metallic glass, Phys. Rev. Lett., 2006, 96: 105503.
[32] H.J. Leamy, H.S. Chen, T.T. Wang, Plastic flow and fracture of metallic glass, Metall. Trans., 1972, 3: 699-708.
[33] A. Inoue, Y. Kawamura, Y. Saotome, High strain rate superplasticity of supercooled liquid for amorphous alloys, Mater. Sci. Forum, 1997, 233-234: 147-154.
[34] Kawamura Y., Shibata T., Inoue A., Masumoto T., Workability of the supercooled liquid in the Zr_(65)Al_(10)Ni_(10)Cu_(15) bulk metallic glass, Acta Mater., 1998, 46: 253-263.
[35] H. Jones, Rapid solidification of metals and alloys, Inst. of Metallurgists, London, 1982.
[36] A. Inoue, T. Zhang, W. Zhang, A. Takeuchi, Bulk Nd-Fe-Al amorphous alloys with hard magnetic properties, Mater. Trans. JIM, 1996, 37: 99-108.
[37] A. Inoue, T. Zhang, A. Takeuchi, W. Zhang, Hard Magnetic Bulk Amorphous Nd-Fe-Al Alloys of 12 mm in Diameter Made by Suction Casting, Mater. Trans. JIM, 1996, 37: 636-640.
[38] A. Inoue, A. Takeuchi, Recent progress in bulk glassy alloys, Mater. Trans. JIM, 2002, 43: 1892-1906.
[39] W.H. Wang, C. Dong, C.H. Shek, Bulk metallic glasses, Mater. Sci. Eng. R., 2004, 44: 45-89.
[40] D.M. Herlach, Non-equilibrium solidification of undercooled metallic melts, Mater. Sci. Eng. R., 1994, 12: 177-272.
[41] C.A. Angell, Formation of glass from liquid and biopolymers, Science, 1995, 267: 1924-1935.
[42] Z.P. Lu, Y. Li, S.C.Ng, Reduced glass transition temperature and glass forming ability of bulk glass forming alloys, J. Non-cryst. Solids, 2000, 270: 103-114.
[43] M.H. Cohen, D. Turnbull, Molecular transport in liquids and glasses, J. Chem. Phys., 1959, 31: 1164-1169.
[44] D. Turnbull, M.H. Cohen, Free-volume model of the amorphous phase: glass transition, J. Chem. Phys., 1961, 34: 120-125.
[45] Z.P. Lu, C.T. Liu, A new glass-forming ability criterion for bulk metallic glass, Acta Mater., 2002, 50: 3501-3512.
[46] M. Ouchetto, B. Elouadi, S. Parke, Study of Lanthanide zinc phosphate glasses by differential thermal analysis, Phys. Chem. Glasses, 1991, 32: 22-28.
[47] A. Inoue, T. Zhang, T. Masumoto, Glass-forming ability of alloys, J. Non-cryst. Solids, 1993, 156-158: 473-480.
[48] T.A. Waniuk, J. Schroers, W.L. Johnson, Critical cooling rate and thermal stability of Zr-Ti-Cu-Ni-Be alloys, Appl. Phys. Lett., 2001, 78: 1213-1215.
[49] Z.P. Lu, C.T. Liu, Glass formation criterion for various glass-forming systems, Phys. Rev. Lett., 2003, 91: 115515.
[50] T. Egami, V. Vitek, D. Srolovitz, in Rapidly Quenched Metals IV, ed. by T. Masumoto, K. Suzuki, Japan Inst. Met., Sendai, 1981.
[51] A. Inoue, Preparation and novel properties of nanocrystalline and nanoquasicrystalline alloys, Nanostruct. Mater., 1995, 6: 53-64.
[52] F. Spaepen, A microscopic mechanism for steady state inhomogeneous flow in metallic glasses, Acta Metall., 1977, 25: 407-415.
[53] D. Turnbull, Under what conditions can a glass be formed?, Contemp. Phys., 1969, 10: 473-488.
[54] M.H. Cohen, G.S. Grest, Liquid-glass transition, a free-volume approach, Phys. Rev. B, 1979, 20: 1077-1098.
[55] P.G. Debenedetti, F.H. Stillinger, Supercooled liquids and the glass transition, Nature, 2001, 410: 259-267.
[56] K.M. Flores, D. Suh, R.H. Dauskardt, P. Asoka-Kumar, P.A. Sterne, R.H. Howell, Characterization of free volume in a bulk metallic glass using positron annihilation spectroscopy, J. Mater. Res., 2002, 17: 1153-1161.
[57] P.S. Steif, F. Spaepen, J.W. Prevost, Strain localization in amorphous metals, Acta Metall., 1982, 30: 447-455.
[58] A.S. Argon, Plastic deformation in metallic glasses, Acta Metall., 1979, 27: 47-58.
[59] R. Huang, Z. Suo, J.H. Prevost, W.D. Nix, Inhomogeneous deformation in metallic glasses, J. Mech. Phys. Solids, 2002, 50: 1011-1027.
[60] W.J. Wright, R.B. Schwarz, W.D. Nix, Localized heating during serrated plastic flow in bulk metallic glasses, Mater. Sci. Eng. A, 2001, 319-321: 229-232.
[61] J.J. Kim, Y. Choi, S. Suresh, A.S. Argon, Nanocrystallization during nanoindentation of a bulk amorphous metal alloy at room temperature, Science, 2002, 295: 654-657.
[62] H.A. Bruck, A.J. Rosakis, W.L. Johnson, The dynamic compressive behavior of beryllium bearing bulk metallic glasses, J. Mater. Res., 1996, 11: 503-511.
[63] K.M. Flores, R.H. Dauskardt, Mean stress effects on flow localization and failure ina bulk metallic glass, Acta Mater., 2001, 49: 2527-2537.
[64] J.J. Lewandowski, A.L. Greer, Temperature rise at shear bands in metallic glasses, Nature Mater., 2006, 5: 15-18.
[65] Q.K. Li, M. Li, Atomic scale characterization of shear bands in an amorphous metal, Appl. Phys. Lett., 2006, 88: 241903.
[66] M.C. Gao, R.E. Hackenberg, G.J. Shiflet, Deformation-induced nanocrystal precipitation in Al-base metallic glasses, Mater. Trans. JIM, 2001, 42: 1741-1747.
[67] Y. He, G.J. Shiflet, S.J. Poon, Ball milling-induced nanocrystal formation in aluminum-based metallic glasses, Acta Metall., 1995, 43: 83-91.
[68] H. Chen, Y. He, G.J. Shiflet, S.J. Poon, Deformation-induced nanocrystal formation in shear bands of amorphous alloys, Nature, 1994, 367: 541-543.
[69] W.H. Jiang, M. Atzmon, The effect of compression and tension on shear-band structure and nanocrystallization in amorphous Al_(90)Fe_5Ga_5: a high-resolution transmission electron microscopy study, Acta Mater., 2003, 51: 4095-4105.
[70] W.H. Jiang, F.E. Pinkerton, M. Atzmon, Deformation-induced nanocrystallization in an Al-based amorphous alloy at subambient temperature, 2003, 48: 1195-1200.
[71] D.V. Louzguine, A. Inoue, Nanocrystallization of Cu-(Zr or Hf)-Ti metallic glasses, J. Mater. Res., 2002, 17: 2112-2120.
[72] M.W. Chen, A. Inoue, W. Zhang, T. Sakurai, Extraordinary plasticity of ductile bulk metallic glasses, Phys. Rev. Lett., 2006, 96: 245502.
[73] R.J. Hebert, J.H. Perepezko, Effect of cold-rolling on the crystallization behavior of amorphous Al_(88)Y_7Fe_5 alloy, Mater. Sci. Eng. A, 2004, 375-377: 728-732.
[74] W.L. Johnson, Thermodynamic and kinetic aspects of the crystal to glass transformation in metallic materials, Prog. Mater. Sci., 1986, 30: 81-134.
[75] A. Inoue, Bulk amorphous alloys-preparation and fundamental characteristics, Trans Tech Publications Ltd., Switzerland, 1998.
[76] H.S. Chen, Stored energy in a cold-rolled metallic glass, Appl. Phys. Lett., 1976, 29:328-330.
[77] J. Das, M.B. Tang, K.B. Kim, R. Theissmann, F. Baier, W.H. Wang, J. Eckert, “Work-hardenable ” ductile bulk metallic glass, Phys. Rev. Lett. 2005, 94: 205501.
[78] D.H. Xu, B. Lohwongwatana, G. Duan, W.L. Johnson, C. Garland, Bulk metallic glass formation in binary Cu-rich alloy series – Cu_(100-x)Zr_x (x = 34, 36, 38.2, 40 at.%) and mechanical properties of bulk Cu_(64)Zr_(36) glass, Acta Mater., 2004, 52: 2621-2624.
[79] G. Duan, D.H. Xu, W.L. Johnson, High copper content bulk glass formation in bimetallic Cu-Hf system, Metall. Mater. Trans. A, 2005, 36: 455-458.
[80] S. Sastry, The relationship between fragility, configurational entropy and the potential energy landscape of glass-forming liquids, Nature, 2001, 409: 164-167.
[81] W.L. Johnson, J. Lu, M.D. Demetriou, Deformation and flow in bulk metallic glasses and deeply undercooled glass forming liquids – a self consistent dynamic free volume model, Intermetallics, 2002, 10: 1039-1046.
[82] W. Kauzmann, The Nature of the glassy state and the behavior of liquids at low temperatures, Chem. Rev., 1948, 43: 219-256.
[83] J. Jackle, Models of the glass transition, Rep. Prog. Phys., 1986, 49: 171-231.
[84] M. Lasocka, The effect of scanning rate on glass transition temperature of splat-cooled Te_(85)Ge_(15), Mater. Sci. Eng., 1976, 23: 173-177.
[85] R. Bruning, K. Samwer, Glass transition on long time scales, Phys. Rev. B, 1992, 46:11318-11322.
[86] T.A. Waniuk, R. Busch, A. Masuhr, W.L. Johnson, Equilibrium viscosity of the Zr_(41.2)Ti_(13.8)Cu_(12.5)Ni_(10)Be_(22.5) bulk metallic glass-forming liquid and viscous flow during relaxation, phase separation, and primary crystallization, Acta Mater., 1998, 46: 5229-5236.
[87] R. Busch, E. Bakke, W.L. Johnson, Viscosity of the supercooled liquid and relaxation at the glass transition of the Zr_(46.75)Ti_(8.25)Cu_(7.5)Ni_(10)Be_(27.5) bulk metallic glass forming alloy, Acta Mater., 1998, 46: 4725-4732.
[88] R. Busch, W. Liu, W.L. Johnson, Thermodynamics and kinetics of the Mg65Cu25Y10 bulk metallic glass forming liquid, J. Appl. Phys., 1998, 83: 4134-4141.
[89] Z.P. Lu, Y. Li, C.T. Liu, Glass-forming tendency of bulk La-Al-Ni-Cu-(Co) metallic glass-forming liquids, J. Appl. Phys., 2003, 93: 286-290.
[90] L. Shadowspeaker, R. Busch, On the fragility of Nb-Ni-based and Zr-based bulk metallic glasses, Appl. Phys. Lett., 2004, 85: 2508-2510.
[91] R. Busch, A. Masuhr, W.L. Johnson, Thermodynamics and kinetics of Zr–Ti–Cu–Ni-Be bulk metallic glass forming liquids, Mater. Sci. Eng. A, 2001, 304-306: 97-102.
[92] S.C. Glade, W.L. Johnson, Viscous flow of the Cu_(47)Ti_(34)Zr_(11)Ni_8 glass forming alloy, J. Appl. Phys., 2000, 87: 7249-7251.
[93] G. Wilde, G.P. Gorler, R. Willnecker, H.J. Frecht, Calorimetric, thermomechanical, and rheological characterizations of bulk glass-forming Pd_(40)Ni_(40)P_(20), J. Appl. Phys., 2000, 87:1141-1152.
[94] K. Kawamura, A. Inoue, Newtonian viscosity of supercooled liquid in a Pd_(40)Ni_(40)P_(20) metallic glass, Appl. Phys. Lett., 2000, 77: 1114-1116.
[95] N. Nishiyama, A. Inoue, Flux treated Pd-Cu-Ni-P amorphous alloy having low critical cooling rate, Mater. Trans. JIM, 1997, 38: 464-472.
[96] R. Elliott, in: Eutectic solidification processing, crystalline and glassy alloy. Bodmin, (Cornwall): Robert Hartnoll; 1983. p.38.
[97] X.H. Lin, W.L. Johnson, Formation of Ti-Zr-Cu-Ni bulk metallic glasses, J. Appl. Phys., 1995, 78: 6514-6519.
[98] T. Zhang, A. Inoue, Preparation of Ti-Cu-Ni-Si-B amorphous alloys with a large supercooled liquid region, Mater. Trans., JIM, 1999, 40: 301.
[99] C. Li, J. Saida, M. Kiminami, A. Inoue, Dynamic crystallization process in a supercooled liquid region of Cu_(40)Ti_(30)Ni_(15)Zr_(10)Sn_5 amorphous alloy, J Non-Cryst Solids, 2000, 261: 108-114.
[100] A. Inoue, W. Zhang, T. Zhang,, K. Kurosaka, Thermal and mechanical properties of Cu-based Cu-Zr-Ti bulk glassy alloys, Mater. Trans. 2001, 42: 1149-1151.
[101] A. Inoue, W. Zhang, T. Zhang, K. Kurosaka, Formation and mechanical properties of Cu-Hf-Ti bulk glassy alloys, J. Mater. Res. 2001, 16: 2836-2844.
[102] A. Inoue, W. Zhang, T. Zhang, K. Kurosaka, Cu-based bulk glassy alloys with good mechanical properties in Cu-Zr-Hf-Ti system, Mater. Trans. 2001, 42: 1805-1812.
[103] J.Z. Jiang, H. Kato, T. Ohsuna, J. Saida, A. Inoue, K. Saksl, H. Franz, K. Stahl, Origin of nondetectable x-ray diffraction peaks in nanocomposite CuTiZr alloys, Appl. Phys. Lett., 2003, 83: 3299-3301.
[104] J.Z. Jiang, B. Yang, K. Saksl, H. Franz, N. Pryds, Crystallization of Cu_(60)Ti_(20)Zr_(20) metallic glass with and without pressure, J. Mater. Res., 2003, 18: 895-898.
[105] A. Concustell, A. Revesz, S. Surinach, M.D. Baro, L.K. Varga, G. Heunen, Microstructural evolution during decomposition and crystallization of the Cu_(60)Zr_(20)Ti_(20) amorphous alloy, J. Mater. Res., 2004, 19: 505-512.
[106] W.A. Johnson, R.F. Mehl, Reaction kinetics in processes of nucleation and growth, Trans. Am. Inst. Min. Metall. Pet. Eng., 1939, 135: 416-458.
[107] M. Avrami, Granulation, phase change and microstructure. Kinetics of phase change. III., J. Chem. Phys., 1941, 9: 177-184.
[108] J.W. Christian, The theory of transformation in metals and alloys, Pergamon Press, Oxford, 2002.
[109] 徐祖耀,相变原理,科学出版社,2000.
[110] J.Z. Jiang, Y.X. Zhuang, H. Rasmussen, J. Saida, A. Inoue, Formation of quasicrystals and amorphous-to-quasicrystalline phase transformation kinetics in Zr_(65)Al_(7.5)Ni_(10)Cu_(7.5)Ag_(10) metallic glass under pressure, Phys. Rev. B, 2001, 64: 094208.
[111] J.B. Zeldovich, On the theory of new phase formation; cavitation., Acta Physicochim URSS, 1943, 18: 1-22.
[112] D. Kashchiev, Solution of non-steady problem in nucleation kinetics, Surf. Sci., 1969, 14: 209-214.
[113] K. Lu, X.D. Liu, F.H. Yuan, Synthesis of the NiZr_2 intermetallic compound nanophase materials, Physica B, 1996, 217: 153-159.
[114] K.F. Kelton, Crystal Nucleation in Liquids and Glasses, Solid State Phys., 1991, 45: 75-178.
[115] D. Turnbull, in: Physics of non-crystalline solids, J.A. Prins (Ed.), North-Holland, Amsterdam, 1964.
[116] H.S. Chen, S.Y. Chuang, Phys. Stat. Sol. A, 1974, 25: 581.
[117] D. Holland-Moritz, Short-range order and solid-liquid interface in undercooled metallic melts, Mater. Sci. Eng. A, 2001, 304-306: 108-113.
[118] F. Spaepen, Structural model for the solid-liquid interface in monatomic systems, Acta Metall., 1975, 23: 729-743.
[119] F. Spaepen, R.B. Meyer, Surface tension in a structural model for the liquid-liquid interface, Scripta Metall., 1976, 10: 37-43.
[120] F. Ye, K. Lu, Pressure effect on polymorphous crystallization kinetics in amorphous selenium, Acta Mater., 1998, 46: 5965-5971.
[121] F. Zhou, R. Luck, K. Lu, E.J. Lavernia, M. Ruhle, Amorphous-to-crystalline transformation induced by thermal annealing of a metastable Al_(90)Fe_(10) composite, Phil. Mag. A, 2002, 82: 1003-1015.
[122] Y.X. Zhuang, J.Z. Jiang, Z.G. Lin, M. Mezouar, W. Crichton, A. Inoue, Evidence of eutectic crystallization and transient nucleation in Al_(89)La_6Ni_5 amorphous alloy, Appl. Phys. Lett., 2001, 79: 743-745.
[123] R. Arroyave, T.W. Eagar, L. Kaufman, Thermodynamic assessment of the Cu-Ti-Zr system, J. Alloys Comp., 2003, 351: 158-170.
[124] A.R. Miedema, F.J.A. den Broeder, On the interfacial energy in solid-liquid and solid-solid metal combination, Z. Metallkd., 1979, 70: 14-20.
[125] H.E. Kissinger, Variation of peak temperature with heating rate in differential thermal analysis, J. Res. Natl Bur. Stand., 1956, 57: 217-221.
[126] Y.Q. Gao, W. Wang, On the activation energy of crystallization in metallic glasses, J. Non-Cryst. Solids, 1986, 81: 129-134.
[127] A.T.W. Kempen, F. Sommer, E.J. Mittemeijer, Determination and interpretation of isothermal and non-isothermal transformation kinetics: the effective activation energies in terms of nucleation and growth, J. Mater. Sci., 2002, 37: 1321-1332.
[128] A.T.W. Kempen, F. Sommer, E.J. Mittemeijer, The isothermal and isochronal kinetics of the crystallisation of bulk amorphous Pd_(40)Cu_(30)P_(20)Ni_(10), Acta Mater., 2002, 50: 1319-1329.
[129] S. Ranganathan, M. von Heimendahl, Three activation energies with isothermal transformation: Applications to metallic glasses, J. Mater. Sci., 1981, 16: 2401-2404.
[130] Y.X. Zhuang, W.H. Wang, Y. Zhang, M.X. Pan, D.Q. Zhao, Crystallization kinetics and glass transition of Zr_(41)Ti_(14)Cu_(12.5)Ni_(10-x)Fe_xBe_(22.5) bulk metallic glasses, Appl. Phys. Lett., 1999, 75: 2392-2394.
[131] B.G. Bagley, E.M. Vogel, Crystallization kinetics of glassy Pd_(0.775)Cu_(0.06)Si_(0.165), J. Non-Cryst. Solids, 1975, 18: 29-32.
[132] M.V. Susic, P.B. Budberg, S.P. Alisova, Kinetics of thermal devitrification (crystallization) of a titanium amorphous alloy, J. Mater. Sci., 1986, 21: 1297-1300.
[133] L. Liu, Z.F. Wu, L. Chen, A kinetic study of the non-isothermal crystallization of a Zr-based bulk metallic glass, Chin. Phys. Lett., 2002, 19: 1483-1486.
[134] F.R. de Boer, R. Boom, W.C.M. Matterns, A.R. Miedena, A.K. Niessen, Cohesion in Metals, Elsevier Science, Amsterdam, 1989.
[135] W.L. Johnson, Bulk glass-forming metallic alloys: science and technology, MRS Bull., 1999, 24: 42-56.
[136] 周玉、武高辉,材料分析测试技术,哈尔滨工业大学出版社,1998.
[137] B.J. Park, H.J. Chang, D.H. Kim, W.T. Kim, In situ formation of two amorphousphases by liquid phase separation in Y-Ti-Al-Co alloy, Appl Phys Lett 2004;85:6353.
[138] S. Schneider, P. Thiyagarajan, W.L. Johnson, Formation of nanocrystals based on decomposition in the amorphous Zr_(41.2)Ti_(13.8)Cu_(12.5)Ni_(10)Be_(22.5) alloy, Appl. Phys. Lett., 1996, 68: 493-495.
[139] A.A. Kundig, M. Ohnuma, D.H. Ping, T. Ohkubo, K. Hono, In situ formed two-phase metallic glass with surface fractal microstructure, Acta Mater., 2004, 52: 2441-2448.
[140] P. de Hey, J. Sietsma, A. van den Beukel, Structural disordering in amorphous Pd_(40)Ni_(40)P_(20) induced by high temperature deformation, Acta Mater., 1998, 46:5873-5882.
[141] A. van den Beukel, J. Sietsma, Glass transition as a free volume related kinetic phenomenon, Acta Metall., 1990, 38: 383-389.
[142] M. Heggen, F. Spaepen, M. Feuerbacher, Creation and annihilation of free volume during homogeneous flow of a metallic glass, J. Appl. Phys., 2005, 97: 033506.
[143] P.D. Miller, J.M. Gibson, Connecting small-angle diffraction with real-space images by quantitative transmission electron microscopy of amorphous thin-films, Ultramicroscopy, 1998, 74: 221-235.
[144] H.Q. Li, K.X. Tao, C. Fan, P.K. Liaw, H. Choo, Effect of temperature on mechanical behavior of Zr-based bulk metallic glasses, Appl. Phys. Lett., 2006, 89: 041921.
[145] N. Morito, Internal friction study on structure relaxation of a glassy metal Fe_(32)Ni_(36)Cr_(14)P_(12)B_6, Mater. Sci. Eng., 1983, 60: 261-268.
[146] J.D. Eshelby, P.L. Pratt, Note on the heating effect of moving dislocations, Acta Metall., 1956, 4: 560-562.
[147] T. Mukai, T.G. Nieh, Y. Kawamura, A. Inoue, K. Higashi, Dynamic response of a Pd40Ni40P20 bulk metallic glass in tension, Scripta Mater., 2002, 46: 43-47.
[148] W.H. Jiang, M. Atzmon, Mechanical strength of nanocrystalline/amorphous Al_(90)Fe_5Gd_5 composites produced by rolling, Appl. Phys. Lett., 2005, 86: 151916.
[149] H.M. Pollock, D. Maugis, M. Barquins, in: Microindentation Techniques in Materials Science and Engineering, P.J. Blau, B.R. Lawn (Eds.), American Society for Testing and Materials Special Technical Publications 889, Philadelphia, 1986, pp. 47-71.
[150] T. Abe, M. Shimono, K. Hashimoto, K. Hono, H. Onodera, Phase separation and glass-forming abilities of ternary alloys, Scripta Mater., 2006, 55: 421-424.
[151] J.Z. Jiang, W. Roseker, L. Gerward, G. Goerigk, Is there phase separation in Cu_(60)Ti_(20)Zr_(20) alloy?, J. Metastable Nanocrystal Mater., 2005, 24-25: 647-652.
[152] H.S. Kim, S.I. Hong, Model of the ductile-brittle transition of partially crystallized amorphous Al-Ni-Y alloys, Acta Mater., 1999, 47: 2059-2066.
[153] N. Chen, D.V. Louzguine, S. Ranganathan, A. Inoue, Formation ranges of icosahedral, amorphous and crystalline phases in rapidly solidified Ti-Zr-Hf-Ni alloys, Acta Mater., 2005, 53: 759-764.
[154] C. Fan, A. Inoue, Ductility of bulk nanocrystalline composites and metallic glasses at room temperature, Appl. Phys. Lett., 2000, 77: 46-48.
[155] C.C. Hays, C.P. Kim, W.L. Johnson, Microstructure controlled shear band pattern formation and enhanced plasticity of bulk metallic glasses containing in situ formed ductile phase dendrite dispersions, Phys. Rev. Lett., 2000, 84: 2901-2904.
[156] U. Kuhn, J. Eckert, N. Mattern, L. Schultz, ZrNbCuNiAl bulk metallic glass matrix composites containing dendritic bcc phase precipitates, Appl. Phys. Lett., 2002, 80: 2478-2480.
[157] H. Choi-Yim, W.L. Johnson, Bulk metallic glass matrix composites, Appl. Phys. Lett., 1997, 71: 3808-3810.