SPS制备锆基和铜基块体非晶复合材料及强韧化机理研究
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摘要
非晶材料因其具有高强度、高硬度、高耐磨性以及优异的耐蚀和磁性能等，得到了人们广泛的关注，相关研究也不断深入。但是由于非晶材料对成分和冷却速率敏感性很高，使其制备的尺寸受限。此外单相非晶块体材料室温下塑性变形能力差。这严重限制了其作为工程材料的应用。在非晶基体内引入晶体相，可提高塑性。但第二相颗粒的引入会对非晶的形成能力造成影响。因此如何制备大块的高强度高塑性非晶材料已成为把非晶合金应用于工程亟待解决的问题，也是非晶研究工作中的关注焦点。
放电等离子烧结(Spark Plasma Sintering, SPS)技术可实现短时快速烧结，可有效避免非晶晶化和增强相影响基体非晶形成能力等诸多问题，非常适合制备大块非晶复合材料。此外，尽管目前很多研究工作集中在利用复合法提高非晶塑性变形能力，但是对其增韧机理，特别是增强相和非晶基体的性能对复合材料力学行为的影响机制的认识尚不够全面。
本文利用SPS技术成功制备了大块的TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5、ZrO_2/Zr_(55)Cu_(30)Al_(10)Ni_5和TiNb/Cu_(46)Zr_(42)Al_7Y_5非晶复合材料。系统地研究了增强相(延性TiNb金属颗粒和硬脆ZrO_2陶瓷颗粒)对非晶基体结构和热稳定性的影响；分析研究了增强相与非晶基体界面结合情况；重点考察了三种非晶基复合材料的力学行为；深入讨论了两种增强相和两种非晶基体性能的差异对非晶基复合材料力学性能的影响；利用有限元模拟的方法并结合复合材料力学性能的结果，研究了复合材料在变形过程中增强相与非晶基体间的应力、应变场的变化。全面地揭示了增强相体积分数、颗粒尺寸和力学性能以及非晶基体的断裂韧性对非晶复合材料力学行为的影响机理。主要研究结果如下：
系统地研究了SPS烧结过程中温度对非晶合金致密化程度和强度的影响规律。研究表明烧结温度与烧结非晶试样的致密化程度和强度均呈非线性关系。烧结温度存在一最佳值，当烧结温度在此值以下时，烧结试样的致密化程度和强度随烧结温度的增加而增加；当烧结温度高于此值时，材料的强度会因非晶试样内缺陷浓度的增加和脆性晶体相的析出而急剧降低。Cu_(46)Zr_(42)Al_7Y_5非晶最佳烧结温度为653K，此时能够得到直径为15mm的非晶试样(铜模铸造法得到的最大尺寸为10mm)，且烧结试样的相对密度可达到99.98%，强度达到1803MPa；Zr_(55)Cu_(30)Al_(10)Ni_5非晶的最佳烧结温度为623K。此时相对密度达到99.85%，强度为1677MPa。均达到了与铜模铸造非晶试样相当的压缩强度。
使用上述经过优化的工艺条件成功制备了TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5、ZrO_2/Zr_(55)Cu_(30)Al_(10)Ni_5和TiNb/Cu_(46)Zr_(42)Al_7Y_5非晶复合材料。并对复合材料的致密化程度、结构、热力学性能以及增强相和非晶基体结合的界面等进行了系统的评价。研究结果表明，采用SPS烧结的方法可以制得致密的非晶复合材料。添加颗粒对非晶基体的结构和热稳定性没有影响，使其保持了完全的非晶相结构特征。透射电镜和纳米压痕分析表明增强相与非晶基体的界面清晰且结合紧密。
全面地考察了增强相的体积分数和颗粒尺寸与复合材料力学性能的关系。Zr_(55)Cu_(30)Al_(10)Ni基体中添加第二相颗粒后，断裂强度得到提高。对于TiNb增韧的非晶复合材料，其塑性应变量随TiNb体积分数的增加而增加。当TiNb含量为30vol.%时，TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5复合材料的塑性应变量达到了11%。而ZrO_2颗粒增韧的非晶复合材料的塑性应变量却随ZrO_2颗粒含量的增加呈现先增加后降低的现象，其最佳增韧效果的体积分数为10-15vol.%。此外，研究结果表明非晶复合材料的塑性应变量还与增强相的颗粒尺寸相关，小尺寸的增强相具有更好的增韧非晶的效果。
研究了增强相增韧非晶的机理。利用有限元模拟的方法深入研究了非晶复合材料压缩过程中增强相、非晶基体以及两者界面处应力和应变场的变化。并结合TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5复合材料的力学行为，全面地揭示了增强相增韧非晶基复合材料的机理。研究结果表明由于在压缩过程中增强相颗粒与非晶基体间存在应变的不匹配，导致两者界面处产生应力集中，界面处高的应力值可诱发非晶基体内剪切带的萌生。增强相颗粒含量的增加意味着非晶基体中更多的剪切带被开动，因而使非晶复合材料具有了更高的塑性应变值。而增强相体积分数相同的情况下，小的颗粒意味着引入第二相在非晶基体内分布更加均匀，增强相与非晶基体的界面更多。因此小尺寸的增强相具有了更好的增韧效果。
比较分析了延性金属颗粒(TiNb)和硬脆陶瓷颗粒(ZrO_2)力学性能对复合材料力学行为的影响。两种颗粒与非晶基体间均存在应变的不匹配，导致界面处应力集中而诱发剪切带产生。只是ZrO_2颗粒只具有弹性变形，它与非晶基体间以弹性应变的不匹配为主。而TiNb颗粒因其具有较强的塑性变形能力，它与非晶基体间除了弹性应变不匹配外，还存在塑性应变的不匹配，可在TiNb与非晶基体间的界面处引入更大的应力集中，从而使非晶基体内剪切带持续增殖，更多的剪切带在TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5复合材料中产生，因此TiNb颗粒有较ZrO_2颗粒更好的增韧效果。
非晶基体断裂韧性是影响非晶基复合材料力学行为的重要因素。断裂韧性值较低的Cu_(46)Zr_(42)Al_7Y_5非晶对裂纹较敏感，一旦在非晶基体内产生裂纹便会迅速扩展导致材料的失效，增强相对其塑性和强度的提高作用有限。而对于断裂韧性值较高的Zr_(55)Cu_(30)Al_(10)Ni_5非晶，由于其对裂纹具有较高的抵御能力，且在应力作用下裂纹尖端应力集中可诱发剪切带的萌生，使裂纹能量降低，同时大量剪切带的萌生可导致微裂纹形成，可使主裂纹运动方向发生偏转，从而延缓了裂纹的扩展，添加TiNb颗粒后其塑性与强度均可得到明显改善。
总之，本文制备得到了高强度、高塑性的非晶复合材料，并深入研究了增强相和非晶基体性能对非晶基复合材料力学行为的影响机理。为制备高强度高塑性非晶基复合材料提供设计思路和理论指导。
Bulk metallic glasses (BMGs) exhibit particular advantages, such as high strength,high hardness, high wear-resistance, superior corrosion resistance and magneticproperties. However, they are unsuitable for structural applications, because most ofBMGs display very limited dimension and plasticity at room. Therefore, how toimprove the plasticity of BMGs with high strength is a key issue for the study ofBMGs.
The plasticity of BMGs can be improved by introducing second phases into themetallic glassy matrix. For the methods of fabricating bulk metallic glassy composites(BMGCs), casting techniques were adopted by most of the researchers, which limits thedimension and affects the glassy formation ability (GFA) of BMGCs. Therefore, thedevelopment of appropriate techniques to fabricate large-size BMGCs is necessary.Spark Plasma Sintering (SPS) is regarded as an appropriate method of fabricatingBMGCs, because BMGCs can be obtained by SPS at low temperature and shortsintering time. On the other hand, although a number of works focus on the research ofBMGCs, the deformation mechanism of BMGs reinforced by the second phases isinsufficient. Especially, the study on the effect of the properties of reinforcement andglassy matrix on the mechanical properties of BMGCs is limited.
In this study, TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5, ZrO_2/Zr_(55)Cu_(30)Al_(10)Ni_5andTiNb/Cu_(46)Zr_(42)Al_7Y_5bulk metallic composites were fabricated by SPS. The structuresand thermal properties of the BMGCs were studied. Meanwhile, the interface betweenthe reinforcement and the glassy matrix was observed. Finite element analysis wasadopted to study the stress field and strain field of the reinforcement, the glassy matrixand the interfaces between them during compression deformation. The effects of volume fraction, particle size and properties of reinforcements as well as the fracturetoughness of the glassy matrix on the mechanical properties of BMGCs were studiedsystematically. The strengthening and toughening mechanism of BMGCs withreinforcements were revealed. The results are summarized as follows.
The influence of sintering temperature on the densities and strength of BMGswere studied. The results indicated that the density and strength of BMGs arenon-linear related to the sintering temperature. There is the optimum sinteringtemperature. When the sintering temperature is below this temperature, the strength anddensity increase with sintering temperature. However, when the sintering temperature isover this temperature, the strength and density of BMGs decrease with sinteringtemperature, because much more defects and crystalline phases are generated.Cu_(46)Zr_(42)Al_7Y_5metallic glass with99.85%relative density was obtained by SPS with adiameter of15mm, which was larger than the largest size of10mm for the as-castspecimen. The fracture strength of the sintered specimen reached1803MPa. Andlarge-size Zr_(55)Cu_(30)Al_(10)Ni_5bulk metallic glass with fracture strength1677MPa wasobtained at623K.
Based on the process of fabricating Cu_(46)Zr_(42)Al_7Y_5and Zr_(55)Cu_(30)Al_(10)Ni_5specimens,TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5, ZrO_2/Zr_(55)Cu_(30)Al_(10)Ni_5and TiNb/Cu_(46)Zr_(42)Al_7Y_5bulk metallicglassy composites were fabricated. And the densities, structures, thermal properties andthe interfaces of the composites were studied. The results indicated that the BMGCswith nearly full density can be obtained by SPS. Meanwhile, the amorphous structureand thermal stability of the glassy matrix were not influenced by the reinforcements. Agood bonding interface between the reinforcement and the glassy matrix was observedby TEM and nano-indentation.
The relationships of the mechanical properties of BMGCs to volume fraction andparticle sizes were studied. For the BMGCs reinforced by TiNb, the plasticity strainincrease with TiNb volume fraction.11%plasticity strain was achieved for30vol.%TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5during compression. However, for the BMGCs reinforced byZrO_2, the largest plasticity strain was achieved with10-15vol.%ZrO_2particles. Both ofBMGCs with TiNb and ZrO_2, larger plasticity was achieved with smaller particle size.
Finite element analysis was adopted to study the stress fields and stress fields ofthe reinforcement, glassy matrix and the interface between them. The results showed that the stress concentration is introduced due to the strain misfit betweenreinforcement and the glassy matrix during compression, which results in the initiationof shear bands in the glassy matrix. Based on the point mentioned above, that largevolume fraction reinforcement and smaller particle size mean more stress concentrationbeing introduced. Therefore, larger plasticity strain was obtained in BMGCs with largervolume fraction or smaller particle size.
The mechanical properties of BMGCs with ductile metal (TiNb) and hard ceramicphase (ZrO_2) were compared. In order to explain the influence of properties ofreinforcements on the mechanical properties of BMGCs, the computational simulationwas adopted. The results indicated that since there are lower yield strength and largerplasticity of TiNb than that of ZrO_2that a larger degree of misfit strain and larger stressconcentration are obtained in the composites with TiNb particles. Thus, the plasticmisfit strain played a key role for the BMGCs toughening by reinforcement.
The fracture toughness of Cu_(46)Zr_(42)Al_7Y_5and Zr_(55)Cu_(30)Al_(10)Ni_5were tested. And theinfluence of the fracture toughness of the glassy matrix on the mechanical properties ofBMGCs was studied. For the Cu_(46)Zr_(42)Al_7Y_5glassy matrix, it is sensitive to the crack,due to the lower fracture toughness. Once a crack is formed in the glassy matrix, it willdevelop quickly and result in failure of the specimen. However, for the Zr_(55)Cu_(30)Al_(10)Ni_5glassy matrix with higher fracture toughness, when crack is initiated in the glassymatrix, shear bands can be formed at the front of crack due to stress concentration. Itwill decrease the energy of the crack, so the development of crack is hindered.Therefore, the difference of the fracture toughness of the glassy matrixes leads to thedifferent effect of TiNb on toughening BMGs.
In summation, bulk metallic glassy composites with high strength and largeplasticity were fabricated. And strengthening and toughening mechanism ofreinforcement in BMGCs were revealed. The influences of the properties ofreinforcements and the glassy matrix on the mechanical properties were studied. Thestrengthening and toughening mechanisms studied in this work provide a guideline forthe design of high strength and large plasticity bulk metallic glassy composites.
放电等离子烧结(Spark Plasma Sintering, SPS)技术可实现短时快速烧结，可有效避免非晶晶化和增强相影响基体非晶形成能力等诸多问题，非常适合制备大块非晶复合材料。此外，尽管目前很多研究工作集中在利用复合法提高非晶塑性变形能力，但是对其增韧机理，特别是增强相和非晶基体的性能对复合材料力学行为的影响机制的认识尚不够全面。
本文利用SPS技术成功制备了大块的TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5、ZrO_2/Zr_(55)Cu_(30)Al_(10)Ni_5和TiNb/Cu_(46)Zr_(42)Al_7Y_5非晶复合材料。系统地研究了增强相(延性TiNb金属颗粒和硬脆ZrO_2陶瓷颗粒)对非晶基体结构和热稳定性的影响；分析研究了增强相与非晶基体界面结合情况；重点考察了三种非晶基复合材料的力学行为；深入讨论了两种增强相和两种非晶基体性能的差异对非晶基复合材料力学性能的影响；利用有限元模拟的方法并结合复合材料力学性能的结果，研究了复合材料在变形过程中增强相与非晶基体间的应力、应变场的变化。全面地揭示了增强相体积分数、颗粒尺寸和力学性能以及非晶基体的断裂韧性对非晶复合材料力学行为的影响机理。主要研究结果如下：
系统地研究了SPS烧结过程中温度对非晶合金致密化程度和强度的影响规律。研究表明烧结温度与烧结非晶试样的致密化程度和强度均呈非线性关系。烧结温度存在一最佳值，当烧结温度在此值以下时，烧结试样的致密化程度和强度随烧结温度的增加而增加；当烧结温度高于此值时，材料的强度会因非晶试样内缺陷浓度的增加和脆性晶体相的析出而急剧降低。Cu_(46)Zr_(42)Al_7Y_5非晶最佳烧结温度为653K，此时能够得到直径为15mm的非晶试样(铜模铸造法得到的最大尺寸为10mm)，且烧结试样的相对密度可达到99.98%，强度达到1803MPa；Zr_(55)Cu_(30)Al_(10)Ni_5非晶的最佳烧结温度为623K。此时相对密度达到99.85%，强度为1677MPa。均达到了与铜模铸造非晶试样相当的压缩强度。
使用上述经过优化的工艺条件成功制备了TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5、ZrO_2/Zr_(55)Cu_(30)Al_(10)Ni_5和TiNb/Cu_(46)Zr_(42)Al_7Y_5非晶复合材料。并对复合材料的致密化程度、结构、热力学性能以及增强相和非晶基体结合的界面等进行了系统的评价。研究结果表明，采用SPS烧结的方法可以制得致密的非晶复合材料。添加颗粒对非晶基体的结构和热稳定性没有影响，使其保持了完全的非晶相结构特征。透射电镜和纳米压痕分析表明增强相与非晶基体的界面清晰且结合紧密。
全面地考察了增强相的体积分数和颗粒尺寸与复合材料力学性能的关系。Zr_(55)Cu_(30)Al_(10)Ni基体中添加第二相颗粒后，断裂强度得到提高。对于TiNb增韧的非晶复合材料，其塑性应变量随TiNb体积分数的增加而增加。当TiNb含量为30vol.%时，TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5复合材料的塑性应变量达到了11%。而ZrO_2颗粒增韧的非晶复合材料的塑性应变量却随ZrO_2颗粒含量的增加呈现先增加后降低的现象，其最佳增韧效果的体积分数为10-15vol.%。此外，研究结果表明非晶复合材料的塑性应变量还与增强相的颗粒尺寸相关，小尺寸的增强相具有更好的增韧非晶的效果。
研究了增强相增韧非晶的机理。利用有限元模拟的方法深入研究了非晶复合材料压缩过程中增强相、非晶基体以及两者界面处应力和应变场的变化。并结合TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5复合材料的力学行为，全面地揭示了增强相增韧非晶基复合材料的机理。研究结果表明由于在压缩过程中增强相颗粒与非晶基体间存在应变的不匹配，导致两者界面处产生应力集中，界面处高的应力值可诱发非晶基体内剪切带的萌生。增强相颗粒含量的增加意味着非晶基体中更多的剪切带被开动，因而使非晶复合材料具有了更高的塑性应变值。而增强相体积分数相同的情况下，小的颗粒意味着引入第二相在非晶基体内分布更加均匀，增强相与非晶基体的界面更多。因此小尺寸的增强相具有了更好的增韧效果。
比较分析了延性金属颗粒(TiNb)和硬脆陶瓷颗粒(ZrO_2)力学性能对复合材料力学行为的影响。两种颗粒与非晶基体间均存在应变的不匹配，导致界面处应力集中而诱发剪切带产生。只是ZrO_2颗粒只具有弹性变形，它与非晶基体间以弹性应变的不匹配为主。而TiNb颗粒因其具有较强的塑性变形能力，它与非晶基体间除了弹性应变不匹配外，还存在塑性应变的不匹配，可在TiNb与非晶基体间的界面处引入更大的应力集中，从而使非晶基体内剪切带持续增殖，更多的剪切带在TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5复合材料中产生，因此TiNb颗粒有较ZrO_2颗粒更好的增韧效果。
非晶基体断裂韧性是影响非晶基复合材料力学行为的重要因素。断裂韧性值较低的Cu_(46)Zr_(42)Al_7Y_5非晶对裂纹较敏感，一旦在非晶基体内产生裂纹便会迅速扩展导致材料的失效，增强相对其塑性和强度的提高作用有限。而对于断裂韧性值较高的Zr_(55)Cu_(30)Al_(10)Ni_5非晶，由于其对裂纹具有较高的抵御能力，且在应力作用下裂纹尖端应力集中可诱发剪切带的萌生，使裂纹能量降低，同时大量剪切带的萌生可导致微裂纹形成，可使主裂纹运动方向发生偏转，从而延缓了裂纹的扩展，添加TiNb颗粒后其塑性与强度均可得到明显改善。
总之，本文制备得到了高强度、高塑性的非晶复合材料，并深入研究了增强相和非晶基体性能对非晶基复合材料力学行为的影响机理。为制备高强度高塑性非晶基复合材料提供设计思路和理论指导。
Bulk metallic glasses (BMGs) exhibit particular advantages, such as high strength,high hardness, high wear-resistance, superior corrosion resistance and magneticproperties. However, they are unsuitable for structural applications, because most ofBMGs display very limited dimension and plasticity at room. Therefore, how toimprove the plasticity of BMGs with high strength is a key issue for the study ofBMGs.
The plasticity of BMGs can be improved by introducing second phases into themetallic glassy matrix. For the methods of fabricating bulk metallic glassy composites(BMGCs), casting techniques were adopted by most of the researchers, which limits thedimension and affects the glassy formation ability (GFA) of BMGCs. Therefore, thedevelopment of appropriate techniques to fabricate large-size BMGCs is necessary.Spark Plasma Sintering (SPS) is regarded as an appropriate method of fabricatingBMGCs, because BMGCs can be obtained by SPS at low temperature and shortsintering time. On the other hand, although a number of works focus on the research ofBMGCs, the deformation mechanism of BMGs reinforced by the second phases isinsufficient. Especially, the study on the effect of the properties of reinforcement andglassy matrix on the mechanical properties of BMGCs is limited.
In this study, TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5, ZrO_2/Zr_(55)Cu_(30)Al_(10)Ni_5andTiNb/Cu_(46)Zr_(42)Al_7Y_5bulk metallic composites were fabricated by SPS. The structuresand thermal properties of the BMGCs were studied. Meanwhile, the interface betweenthe reinforcement and the glassy matrix was observed. Finite element analysis wasadopted to study the stress field and strain field of the reinforcement, the glassy matrixand the interfaces between them during compression deformation. The effects of volume fraction, particle size and properties of reinforcements as well as the fracturetoughness of the glassy matrix on the mechanical properties of BMGCs were studiedsystematically. The strengthening and toughening mechanism of BMGCs withreinforcements were revealed. The results are summarized as follows.
The influence of sintering temperature on the densities and strength of BMGswere studied. The results indicated that the density and strength of BMGs arenon-linear related to the sintering temperature. There is the optimum sinteringtemperature. When the sintering temperature is below this temperature, the strength anddensity increase with sintering temperature. However, when the sintering temperature isover this temperature, the strength and density of BMGs decrease with sinteringtemperature, because much more defects and crystalline phases are generated.Cu_(46)Zr_(42)Al_7Y_5metallic glass with99.85%relative density was obtained by SPS with adiameter of15mm, which was larger than the largest size of10mm for the as-castspecimen. The fracture strength of the sintered specimen reached1803MPa. Andlarge-size Zr_(55)Cu_(30)Al_(10)Ni_5bulk metallic glass with fracture strength1677MPa wasobtained at623K.
Based on the process of fabricating Cu_(46)Zr_(42)Al_7Y_5and Zr_(55)Cu_(30)Al_(10)Ni_5specimens,TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5, ZrO_2/Zr_(55)Cu_(30)Al_(10)Ni_5and TiNb/Cu_(46)Zr_(42)Al_7Y_5bulk metallicglassy composites were fabricated. And the densities, structures, thermal properties andthe interfaces of the composites were studied. The results indicated that the BMGCswith nearly full density can be obtained by SPS. Meanwhile, the amorphous structureand thermal stability of the glassy matrix were not influenced by the reinforcements. Agood bonding interface between the reinforcement and the glassy matrix was observedby TEM and nano-indentation.
The relationships of the mechanical properties of BMGCs to volume fraction andparticle sizes were studied. For the BMGCs reinforced by TiNb, the plasticity strainincrease with TiNb volume fraction.11%plasticity strain was achieved for30vol.%TiNb/Zr_(55)Cu_(30)Al_(10)Ni_5during compression. However, for the BMGCs reinforced byZrO_2, the largest plasticity strain was achieved with10-15vol.%ZrO_2particles. Both ofBMGCs with TiNb and ZrO_2, larger plasticity was achieved with smaller particle size.
Finite element analysis was adopted to study the stress fields and stress fields ofthe reinforcement, glassy matrix and the interface between them. The results showed that the stress concentration is introduced due to the strain misfit betweenreinforcement and the glassy matrix during compression, which results in the initiationof shear bands in the glassy matrix. Based on the point mentioned above, that largevolume fraction reinforcement and smaller particle size mean more stress concentrationbeing introduced. Therefore, larger plasticity strain was obtained in BMGCs with largervolume fraction or smaller particle size.
The mechanical properties of BMGCs with ductile metal (TiNb) and hard ceramicphase (ZrO_2) were compared. In order to explain the influence of properties ofreinforcements on the mechanical properties of BMGCs, the computational simulationwas adopted. The results indicated that since there are lower yield strength and largerplasticity of TiNb than that of ZrO_2that a larger degree of misfit strain and larger stressconcentration are obtained in the composites with TiNb particles. Thus, the plasticmisfit strain played a key role for the BMGCs toughening by reinforcement.
The fracture toughness of Cu_(46)Zr_(42)Al_7Y_5and Zr_(55)Cu_(30)Al_(10)Ni_5were tested. And theinfluence of the fracture toughness of the glassy matrix on the mechanical properties ofBMGCs was studied. For the Cu_(46)Zr_(42)Al_7Y_5glassy matrix, it is sensitive to the crack,due to the lower fracture toughness. Once a crack is formed in the glassy matrix, it willdevelop quickly and result in failure of the specimen. However, for the Zr_(55)Cu_(30)Al_(10)Ni_5glassy matrix with higher fracture toughness, when crack is initiated in the glassymatrix, shear bands can be formed at the front of crack due to stress concentration. Itwill decrease the energy of the crack, so the development of crack is hindered.Therefore, the difference of the fracture toughness of the glassy matrixes leads to thedifferent effect of TiNb on toughening BMGs.
In summation, bulk metallic glassy composites with high strength and largeplasticity were fabricated. And strengthening and toughening mechanism ofreinforcement in BMGCs were revealed. The influences of the properties ofreinforcements and the glassy matrix on the mechanical properties were studied. Thestrengthening and toughening mechanisms studied in this work provide a guideline forthe design of high strength and large plasticity bulk metallic glassy composites.
引文
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