Nb、Ta碳/硼化物及Cr、Mo元素对NiAl压缩性能的影响规律及机制
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摘要
NiAl金属间化合物因其具有高熔点、相对较小的密度、较高的强度、较好的导热性能和较好的抗高温氧化性等优点，被视为高温结构材料极有竞争力的候选材料之一，但是由于其室温韧性较差，高温条件下的强度较低。因此，使其实际应用受到一定限制。目前，合成和制备NiAl金属间化合物及其合金的方法有很多，常见的方法有：高温熔炼、自蔓延高温合成、定向凝固、电弧熔炼等等。然而，这些方法或多或少都存在一些不足，例如，熔炼条件苛刻，生产成本高，容易造成成分偏析等。为了改善上述方法带来的缺陷，本论文利用燃烧合成+热压法合成和制备NiAl合金及其复合材料。燃烧合成+热压法是在燃烧合成反应后，样品处于高温状态时，立即对反应物施加压力。这种方法具有操作简单、成本低廉、所制得的合金晶粒细小等特点。
本文利用Ni-Al-Nb-B_4C体系，Ni-Al-Me(Me=Mo，Cr和B)体系，通过燃烧合成+热压法合成制备NiAl合金及NiAl基复合材料，并且研究了陶瓷颗粒的种类、尺寸和合金化元素的种类、含量对NiAl合金室温压缩性能的影响规律；提出了陶瓷颗粒和合金化元素强韧化NiAl的机制。
本文的主要研究结果如下：
(1)发现分别采用Ni-Al、Mo/Cr-Ni-Al、Ni-Al-Nb-B_4C等体系，通过烧合成+热压一体化方法制备的纯NiAl合金，5、10、15at.%的Mo或25、30、35at.%的Cr合金化NiAl合金和5、10、15、20wt.%(NbB_2、Nb_2C、NbC)三相陶瓷颗粒增强NiAl基复合材料的NiAl基体的晶粒尺寸得到非常显著的细化，分别为60-80μm，10-20μm和10-30μm。同时，由于反应速度和凝固过程的冷却速度极快及在压力下成型，产生很大内应力，所以在铸态NiAl基体组织中具有较多位错。
(2)提出了纯NiAl合金、Mo/Cr合金化NiAl合金和(NbB_2、Nb_2C、NbC)三相陶瓷颗粒增强NiAl基复合材料NiAl基体的晶粒细化机制。
a)纯NiAl合金晶粒细化机制：采用Ni-Al体系燃烧合成NiAl金属间化合物在瞬间发生和完成。因此，冷却速度极快，产生很大的过冷度，使临界自发形核的核心尺寸大大减小，使形核几率显著增加，导致晶粒细化。
b) Mo/Cr合金化NiAl合金晶粒细化机制：在Ni-Al燃烧合成体系中添加大量的高熔点第三组元Mo(熔点：2623℃)或Cr(熔点：1863℃)，使体系的最高燃烧温度明显下降，导致NiAl的晶粒尺寸显著细化。
c) Nb_2C、NbB_2和NbC颗粒增强NiAl基复合材料NiAl基体晶粒细化机制：NbB_2的(0001)面和Nb_2C的(0001)面与NiAl基体的(100)面的错配度(δ(%))分别为6.1和6.2%，为半共格关系。因此，NbB_2和Nb_2C可作为NiAl形核的有效异质核心，大幅度增加了NiAl的形核核心数量，使NiAl晶粒得到显著细化。同时，较大尺寸的NbB_2和Nb_2C颗粒陶瓷被推到固液界面前沿，最后分布在NiAl基体的晶界处，起到了阻碍NiAl生长的作用，使NiAl晶粒得到进一步细化。
(3)揭示出纯NiAl合金、Mo/Cr合金化NiAl合金和陶瓷颗粒增强NiAl基复合材料在压缩应变速率为1.0×10~(-4)s~(-1)时具有十分优异的室温压缩力学性能和加工硬化能力。
a)纯NiAl合金的压缩真实屈服强度、断裂强度、断裂应变、加工硬化能力和硬度分别达到419MPa、1005MPa、21.6%、1.40和360HV。
b)在NiAl合金中添加Mo明显地提高室温压缩力学性能，随着Mo含量的提高，性能提高。在分别添加5、10和15at.%的Mo含量中，15at.%Mo的综合性能最好，其真实屈服强度、断裂强度和硬度分别达到747MPa、1619MPa和621HV，分别比纯NiAl提高328MPa、614MPa和261HV，真实断裂应变和加工硬化能力(Hc值)稍有降低，分别从21.6%和1.40降低到20.4%和1.16。
c)在NiAl合金添加Cr，十分明显地提高室温压缩力学性能。在分别添加25、30和35at.%的Cr中30at.%Cr的综合性能最好，其真实屈服强度、断裂强度、断裂应变、加工硬化能力和硬度分别达到809MPa、1909MPa、21.4%、1.35和667HV，其中真实屈服强度、断裂强度和硬度分别比纯NiAl合金提高390MPa、904MPa和307HV，均提高将近一倍。真实断裂应变和加工硬化能力与NiAl合金相当。
d)在(NbB_2、Nb_2C和NbC)三相，(NbB_2和NbC)、(NbB_2和Nb_2C)、(TaB_2和TaB)双相和TaC单相陶瓷颗粒增强的NiAl基复合材料中5.0wt.%三相陶瓷颗粒(NbB_2、Nb_2C和NbC)增强的NiAl基复合材料具有最佳的综合压缩力学性能，其真实断裂屈服强度、断裂强度和硬度分别达到653MPa、1497MPa和466HV，分别比纯NiAl合金提高234MPa、492MPa和106HV，真实断裂应变和加工硬化能力(Hc值)稍有下降，分别从21.6%和1.40降低到18.3%和1.29。
(4)发现纯NiAl合金、Mo/Cr合金化NiAl合金和陶瓷颗粒增强NiAl基复合材料均具有较强的压缩应变速率敏感性。在压缩应变速率由1.25×10~(-2)s~(-1)下降到1.0×10~(-4)s~(-1)时，
a)纯NiAl合金：真实断裂应变和加工硬化能力(Hc值)分别提高8.4%和0.62；真实屈服强度和断裂强度分别降低151MPa和15MPa。
b)30at.%Cr合金化NiAl合金：真实断裂强度、断裂应变和加工硬化能力(Hc值)同时提高，分别提高118MPa、2.7%和0.65，尤其是加工硬化能力提高了93%；真实屈服强度下降245MPa。
c)5.0wt.%三相陶瓷颗粒(NbB_2、Nb_2C和NbC)增强的NiAl基复合材料：真实断裂应变和加工硬化能力同时提高，分别提高6.4%和0.46；真实断裂强度变化不大；真实屈服强度下降149MPa。在压缩应变速率由1.25×10~(-2)s~(-1)下降到5.0×10~(-4)s~(-1)时，15at.%Mo合金化NiAl合金：真实屈服强度、断裂强度、断裂应变和加工硬化能力(Hc值)同时提高，分别提高了46MPa、250MPa、13.7%和0.2，尤其是断裂应变提高一倍以上。
(5)揭示出纯NiAl合金、Mo/Cr合金化NiAl合金和(NbB_2、Nb_2C、NbC)三相陶瓷颗粒增强NiAl基复合材料的强化机制。
a)纯NiAl合金强化机制。采用燃烧合成+热压一体化方法制备的纯NiAl合金的晶粒显著细化，大大提高了强度和断裂应变；NiAl合金存在大量的位错和晶格扭曲。压缩变形过程中位错密度明显提高，压缩前后的位错密度分别为5.08×1011cm-2，5.92×1011cm-2，提高幅度为0.84×1011cm-2，导致强度和加工硬化能力提高。因此，纯NiAl合金的强化机制为：细晶强化。
b) Mo/Cr合金化NiAl合金强化机制：Mo、Cr在NiAl合金中的存在形式为：一部分Mo、Cr固溶到NiAl合金中，使晶格发生畸变；一部分Mo、Cr在NiAl合金基体中析出，其尺寸大约为20-30nm。Mo(170HV)和Cr(115HV)的硬度均低NiAl合金的硬度(360HV)。因此，纯Mo、Cr相为一种软相存在于基体中；一部分Mo、Cr分布在晶界处。因此，添加Mo/Cr的强化机制为：细晶强化、固溶强化和第二相强化。
c)(NbB_2、Nb_2C、NbC)三相陶瓷颗粒增强NiAl基复合材料的强化机制：尺寸大约在1-2μm的NbB_2和Nb_2C分布在NiAl基体中，尺寸大约在40μm的NbB_2、Nb_2C和NbC分布在NiAl基体的晶界处。由于NiAl基体晶粒尺寸的显著细化和NbB_2、Nb_2C和NbC陶瓷颗粒的存在，在压缩变形过程中位错密度显著提高，压缩前后的位错密度分别为8.28×1011cm-2和1.20×1012cm-2，提高幅度为3.72×1011cm-2，导致强度和加工硬化能力提高。因此，NbB_2、Nb_2C和NbC颗粒增强的强化机制为：细晶强化和第二相强化。
总之，本文通过燃烧合成+热压法制备NiAl，NiAl合金以及NiAl基复合材料，研究了其室温压缩性能，揭示了不同制备方法、不同合金化元素含量、不同陶瓷含量对NiAl室温压缩性能的影响规律和机制，为实现NiAl室温压缩性能的提高奠定了必要的理论基础。
Due to the desirable combination of the high melting temperature, high-temperatureoxidation resistance and low density, the NiAl intermetallic compound is regarded as one ofthe most promising candicates for high temperature applications. Howerver, the actual use ofthe NiAl alloy has been limited by the low ductility at room temperature and the inadequatecreep resistance at high temperatures. There are many methods have been developed for thiscompound, including powder processing, casting, arc melting, directional solidification andself-propagating high temperature synthesis. The methods metioned above have somedefects, such as the tough melting condition, high cost, and composition segregation. As toimproving the defects of the methods metioned above, high-temperature combustion reactionand hot press was used for fabricationg the NiAl and NiAl-matrix composite.High-temperature combustion reaction and hot press based on the combustion reaction.When the reation oucurs, a axial force is added. The characteristic of the method is easy, lowcost and the fine grains, and so on.In this paper, the Ni-Al-Nb-B_4C system and the Ni-Al-Me (Me=Mo, Cr and B) are usedfor fabricationg the NiAl matrix composite and NiAl alloys by the high-temperaturecombustion reaction and hot press method. The effect of the kind and the size of the ceramicpartuculates and the kind and the content of the alloying elements on the room-temperaturecompression properties are researched in the paper. The strengthen mechanism of theceramic particulates and the alloying elements for the NiAl was discussed.
The main results are as follows:
(1) Ni-Al, Mo/Cr-Ni-Al, Ni-Al-Nb-B_4C systems were used for fabricating the NiAlalloy, NiAl-xMo(x=5,10and15) alloys, NiAl-xCr(x=25,30and35) alloys andNiAl-matix composite with Nb_2C, NbB_2and NbC by the high-temperature combustion reaction and hot press. All the grains of the NiAl alloys were refined.The grain size of the alloys was about60-80μm,10-20μm and10-30μm,respectively. The alloys were formed in instant, which leads to the rapid cooling.The size of the nucleation reduced, and the alloys were refined. When the reactionoccurs, a aixl force is applied. It can produce a lot of dislocations.
(2) The mechanism of the fine garins in the NiAl, NiAl alloys and NiAl-matrixcomposite was discussed.
a) The mechanism of the pure NiAl: The reaction occurs and finished at one sight,and the cooling degree was very low, which can make the size of the criticalnucleation little. The probability of the nucleation improved, and the grains werefine.
b) The mechanism of the NiAl-Mo/Cr alloys: The addition of the high meltingpoint metals Mo (2623℃) and Cr (1863℃) made the max combustion temperaturedecreased obviously, which can make the grain fine.
c) The mechanism of the NiAl with Nb_2C, NbB_2and NbC: The misfit between the(0001) of Nb_2C and NbB_2and (100) of NiAl are6.1%and6.2%, repectively. So theceramic particulates of Nb_2C and NbB_2were regarded as the nucleation for NiAl. Theamount of the nucleation increased, and the grain became fine.
(3) The NiAl, NiAl-Mo/Cr alloys and the NiAl-matrix composite have goodroom-temperature compression properties and high work-hardening capacity at thestrain rate of1.0×10~(-4)s~(-1).
a) The ture yield strength, fracture strength, the fracture strain, the work-hardeningcapacity and the hardness of the NiAl are419MPa、1005MPa、21.6%、1.40and360HV, respectively.
b) The room-temprature compression properties were improved obviously with theaddition of5,10and15at.%Mo. The compression properties of the NiAl-15Moalloy are the best, and the ture yield strength, fracture strength, and the hardness are747MPa,1619MPa and621HV, respectively. While the ture fracture strain andthe work-hardening capacity are little, lower than those of the pure NiAl.
c) The addition of Cr can improve the compression properties of NiAl alloy.Among the NiAl-xCr alloys, the NiAl alloys with30at.%Cr has the best properties.The ture yield strength, fracture strength, the fracture strain, the work-hardeningcapacity and the hardness of the NiAl-30Cr alloy are809MPa,1909MPa,21.4%,1.35and667HV.390MPa,904MPa and307HV, respectively improve the trueyield strength, the fracture strength and the hardness. The ture fracture strain and the work-hardening capacity is as high as those of the pure NiAl alloy.
d) The compression properties of the NiAl-matrxi composite with5wt.%Nb_2C,NbB_2and NbC are the best among the different content and kind ceramicparticulates reinforced NiAl-matrix composites. The true yield strength, fracturestrength, and the hardness of the composite are653MPa,1497MPa and466HV,repectively. The fracture strain and the work-hardening capacity decreased lightly.
(4) It was found that the NiAl alloy, NiAl-Mo/Cr alloys have strain rate sensitivity.When the strain rate decrease from1.25×10~(-2)s~(-1)to1.0×10~(-4)s~(-1),
a) For NiAl, the fracture strain and the work-hardening capacity are improved by8.4%and0.62, respectively.The true yield strength and the fracture strength aredecreased by151MPa and15MPa, respectively.
b) For NiAl-30Cr alloys, the true fracture strength, fracture strain andwork-hardening capacity improved by118MPa,2.7%and0.65, especially thework-hardening capacity, which is improved by93%, while the yield strengthdecreased245MPa.
c) For NiAl-matrix composite with5wt.%Nb_2C, NbB_2and NbC, both of thestrength and the work-haedening capacity are improved by6.4%and0.46,respectively. The true fracture strength did not changed obviously, and the yieldstrength decreased149MPa.When the compression strain rate decreased from1.25×10~(-2)s~(-1)to5.0×10~(-4)s~(-1), thetrue yield strength, the frcacture strength, the fracture strain and thework-hardening capacity of the NiAl-15Mo alloy were improved by46MPa,250MPa,13.7%and0.2.
(5) The mechanism of the strengthening of the NiAl, NiAl-Mo/Cr, NiAl-matrixcomposite with Nb_2C, NbB_2and NbC was discussed.
a) The mechanism for NiAl, The NiAl fabricated by the high-temperaturecombustion reaction and hot press was refined, and the strength and the fracturestrain are improved. There were many dislocations distributed in the NiAl matrix,and the lattice of the NiAl distorted. The amount of dislactions increased during thecompression processing, from5.08×1011cm-2to5.92×1011cm-2, which canimprove the work-hardening capacity. Therefore, the mechanism for NiAl isfine-grained strengthening.
b) The mechanism of the NiAl-Mo/Cr alloys, Mo and Cr exsit in NiAl as threetypes. A proportion of Mo/Cr solutes to the NiAl, which leads to the latticedistorted. A proportion of Mo/Cr precitipitation in NiAl, and the size is about20-30 nm. As Mo and Cr is soft than NiAl, they exsit in NiAl as a soft phase. Anotherproportion of Cr/Mo distributed at the grain boundaries. The strengtheningmechanisms are fined-grain strengthening, solution strengthening and the secondphase strengthening.
c) The mechanism of the NiAl-matrix composite with5wt.%Nb_2C, NbB_2andNbC: The size of the ceramic paticulates in the grains is about1-2μm, while thesize of the ceramic particulates at the grain boundaries is about40μm. The amountof dislactions increased during the compression processing, from8.28×1011cm-2to1.20×1012cm-2, which can improve the work-hardening capacity. Therefore, themechanism for NiAl-matrix composite with Nb_2C, NbB_2and NbC is fine-grainedstrengthening and the second phase strengthening.
In summary, the effect of the addition of the ceramic and alloying elements on thecompression properties of NiAl was studied in this paper. It can be benifical to theimprovement for the compression properties of NiAl.
本文利用Ni-Al-Nb-B_4C体系，Ni-Al-Me(Me=Mo，Cr和B)体系，通过燃烧合成+热压法合成制备NiAl合金及NiAl基复合材料，并且研究了陶瓷颗粒的种类、尺寸和合金化元素的种类、含量对NiAl合金室温压缩性能的影响规律；提出了陶瓷颗粒和合金化元素强韧化NiAl的机制。
本文的主要研究结果如下：
(1)发现分别采用Ni-Al、Mo/Cr-Ni-Al、Ni-Al-Nb-B_4C等体系，通过烧合成+热压一体化方法制备的纯NiAl合金，5、10、15at.%的Mo或25、30、35at.%的Cr合金化NiAl合金和5、10、15、20wt.%(NbB_2、Nb_2C、NbC)三相陶瓷颗粒增强NiAl基复合材料的NiAl基体的晶粒尺寸得到非常显著的细化，分别为60-80μm，10-20μm和10-30μm。同时，由于反应速度和凝固过程的冷却速度极快及在压力下成型，产生很大内应力，所以在铸态NiAl基体组织中具有较多位错。
(2)提出了纯NiAl合金、Mo/Cr合金化NiAl合金和(NbB_2、Nb_2C、NbC)三相陶瓷颗粒增强NiAl基复合材料NiAl基体的晶粒细化机制。
a)纯NiAl合金晶粒细化机制：采用Ni-Al体系燃烧合成NiAl金属间化合物在瞬间发生和完成。因此，冷却速度极快，产生很大的过冷度，使临界自发形核的核心尺寸大大减小，使形核几率显著增加，导致晶粒细化。
b) Mo/Cr合金化NiAl合金晶粒细化机制：在Ni-Al燃烧合成体系中添加大量的高熔点第三组元Mo(熔点：2623℃)或Cr(熔点：1863℃)，使体系的最高燃烧温度明显下降，导致NiAl的晶粒尺寸显著细化。
c) Nb_2C、NbB_2和NbC颗粒增强NiAl基复合材料NiAl基体晶粒细化机制：NbB_2的(0001)面和Nb_2C的(0001)面与NiAl基体的(100)面的错配度(δ(%))分别为6.1和6.2%，为半共格关系。因此，NbB_2和Nb_2C可作为NiAl形核的有效异质核心，大幅度增加了NiAl的形核核心数量，使NiAl晶粒得到显著细化。同时，较大尺寸的NbB_2和Nb_2C颗粒陶瓷被推到固液界面前沿，最后分布在NiAl基体的晶界处，起到了阻碍NiAl生长的作用，使NiAl晶粒得到进一步细化。
(3)揭示出纯NiAl合金、Mo/Cr合金化NiAl合金和陶瓷颗粒增强NiAl基复合材料在压缩应变速率为1.0×10~(-4)s~(-1)时具有十分优异的室温压缩力学性能和加工硬化能力。
a)纯NiAl合金的压缩真实屈服强度、断裂强度、断裂应变、加工硬化能力和硬度分别达到419MPa、1005MPa、21.6%、1.40和360HV。
b)在NiAl合金中添加Mo明显地提高室温压缩力学性能，随着Mo含量的提高，性能提高。在分别添加5、10和15at.%的Mo含量中，15at.%Mo的综合性能最好，其真实屈服强度、断裂强度和硬度分别达到747MPa、1619MPa和621HV，分别比纯NiAl提高328MPa、614MPa和261HV，真实断裂应变和加工硬化能力(Hc值)稍有降低，分别从21.6%和1.40降低到20.4%和1.16。
c)在NiAl合金添加Cr，十分明显地提高室温压缩力学性能。在分别添加25、30和35at.%的Cr中30at.%Cr的综合性能最好，其真实屈服强度、断裂强度、断裂应变、加工硬化能力和硬度分别达到809MPa、1909MPa、21.4%、1.35和667HV，其中真实屈服强度、断裂强度和硬度分别比纯NiAl合金提高390MPa、904MPa和307HV，均提高将近一倍。真实断裂应变和加工硬化能力与NiAl合金相当。
d)在(NbB_2、Nb_2C和NbC)三相，(NbB_2和NbC)、(NbB_2和Nb_2C)、(TaB_2和TaB)双相和TaC单相陶瓷颗粒增强的NiAl基复合材料中5.0wt.%三相陶瓷颗粒(NbB_2、Nb_2C和NbC)增强的NiAl基复合材料具有最佳的综合压缩力学性能，其真实断裂屈服强度、断裂强度和硬度分别达到653MPa、1497MPa和466HV，分别比纯NiAl合金提高234MPa、492MPa和106HV，真实断裂应变和加工硬化能力(Hc值)稍有下降，分别从21.6%和1.40降低到18.3%和1.29。
(4)发现纯NiAl合金、Mo/Cr合金化NiAl合金和陶瓷颗粒增强NiAl基复合材料均具有较强的压缩应变速率敏感性。在压缩应变速率由1.25×10~(-2)s~(-1)下降到1.0×10~(-4)s~(-1)时，
a)纯NiAl合金：真实断裂应变和加工硬化能力(Hc值)分别提高8.4%和0.62；真实屈服强度和断裂强度分别降低151MPa和15MPa。
b)30at.%Cr合金化NiAl合金：真实断裂强度、断裂应变和加工硬化能力(Hc值)同时提高，分别提高118MPa、2.7%和0.65，尤其是加工硬化能力提高了93%；真实屈服强度下降245MPa。
c)5.0wt.%三相陶瓷颗粒(NbB_2、Nb_2C和NbC)增强的NiAl基复合材料：真实断裂应变和加工硬化能力同时提高，分别提高6.4%和0.46；真实断裂强度变化不大；真实屈服强度下降149MPa。在压缩应变速率由1.25×10~(-2)s~(-1)下降到5.0×10~(-4)s~(-1)时，15at.%Mo合金化NiAl合金：真实屈服强度、断裂强度、断裂应变和加工硬化能力(Hc值)同时提高，分别提高了46MPa、250MPa、13.7%和0.2，尤其是断裂应变提高一倍以上。
(5)揭示出纯NiAl合金、Mo/Cr合金化NiAl合金和(NbB_2、Nb_2C、NbC)三相陶瓷颗粒增强NiAl基复合材料的强化机制。
a)纯NiAl合金强化机制。采用燃烧合成+热压一体化方法制备的纯NiAl合金的晶粒显著细化，大大提高了强度和断裂应变；NiAl合金存在大量的位错和晶格扭曲。压缩变形过程中位错密度明显提高，压缩前后的位错密度分别为5.08×1011cm-2，5.92×1011cm-2，提高幅度为0.84×1011cm-2，导致强度和加工硬化能力提高。因此，纯NiAl合金的强化机制为：细晶强化。
b) Mo/Cr合金化NiAl合金强化机制：Mo、Cr在NiAl合金中的存在形式为：一部分Mo、Cr固溶到NiAl合金中，使晶格发生畸变；一部分Mo、Cr在NiAl合金基体中析出，其尺寸大约为20-30nm。Mo(170HV)和Cr(115HV)的硬度均低NiAl合金的硬度(360HV)。因此，纯Mo、Cr相为一种软相存在于基体中；一部分Mo、Cr分布在晶界处。因此，添加Mo/Cr的强化机制为：细晶强化、固溶强化和第二相强化。
c)(NbB_2、Nb_2C、NbC)三相陶瓷颗粒增强NiAl基复合材料的强化机制：尺寸大约在1-2μm的NbB_2和Nb_2C分布在NiAl基体中，尺寸大约在40μm的NbB_2、Nb_2C和NbC分布在NiAl基体的晶界处。由于NiAl基体晶粒尺寸的显著细化和NbB_2、Nb_2C和NbC陶瓷颗粒的存在，在压缩变形过程中位错密度显著提高，压缩前后的位错密度分别为8.28×1011cm-2和1.20×1012cm-2，提高幅度为3.72×1011cm-2，导致强度和加工硬化能力提高。因此，NbB_2、Nb_2C和NbC颗粒增强的强化机制为：细晶强化和第二相强化。
总之，本文通过燃烧合成+热压法制备NiAl，NiAl合金以及NiAl基复合材料，研究了其室温压缩性能，揭示了不同制备方法、不同合金化元素含量、不同陶瓷含量对NiAl室温压缩性能的影响规律和机制，为实现NiAl室温压缩性能的提高奠定了必要的理论基础。
Due to the desirable combination of the high melting temperature, high-temperatureoxidation resistance and low density, the NiAl intermetallic compound is regarded as one ofthe most promising candicates for high temperature applications. Howerver, the actual use ofthe NiAl alloy has been limited by the low ductility at room temperature and the inadequatecreep resistance at high temperatures. There are many methods have been developed for thiscompound, including powder processing, casting, arc melting, directional solidification andself-propagating high temperature synthesis. The methods metioned above have somedefects, such as the tough melting condition, high cost, and composition segregation. As toimproving the defects of the methods metioned above, high-temperature combustion reactionand hot press was used for fabricationg the NiAl and NiAl-matrix composite.High-temperature combustion reaction and hot press based on the combustion reaction.When the reation oucurs, a axial force is added. The characteristic of the method is easy, lowcost and the fine grains, and so on.In this paper, the Ni-Al-Nb-B_4C system and the Ni-Al-Me (Me=Mo, Cr and B) are usedfor fabricationg the NiAl matrix composite and NiAl alloys by the high-temperaturecombustion reaction and hot press method. The effect of the kind and the size of the ceramicpartuculates and the kind and the content of the alloying elements on the room-temperaturecompression properties are researched in the paper. The strengthen mechanism of theceramic particulates and the alloying elements for the NiAl was discussed.
The main results are as follows:
(1) Ni-Al, Mo/Cr-Ni-Al, Ni-Al-Nb-B_4C systems were used for fabricating the NiAlalloy, NiAl-xMo(x=5,10and15) alloys, NiAl-xCr(x=25,30and35) alloys andNiAl-matix composite with Nb_2C, NbB_2and NbC by the high-temperature combustion reaction and hot press. All the grains of the NiAl alloys were refined.The grain size of the alloys was about60-80μm,10-20μm and10-30μm,respectively. The alloys were formed in instant, which leads to the rapid cooling.The size of the nucleation reduced, and the alloys were refined. When the reactionoccurs, a aixl force is applied. It can produce a lot of dislocations.
(2) The mechanism of the fine garins in the NiAl, NiAl alloys and NiAl-matrixcomposite was discussed.
a) The mechanism of the pure NiAl: The reaction occurs and finished at one sight,and the cooling degree was very low, which can make the size of the criticalnucleation little. The probability of the nucleation improved, and the grains werefine.
b) The mechanism of the NiAl-Mo/Cr alloys: The addition of the high meltingpoint metals Mo (2623℃) and Cr (1863℃) made the max combustion temperaturedecreased obviously, which can make the grain fine.
c) The mechanism of the NiAl with Nb_2C, NbB_2and NbC: The misfit between the(0001) of Nb_2C and NbB_2and (100) of NiAl are6.1%and6.2%, repectively. So theceramic particulates of Nb_2C and NbB_2were regarded as the nucleation for NiAl. Theamount of the nucleation increased, and the grain became fine.
(3) The NiAl, NiAl-Mo/Cr alloys and the NiAl-matrix composite have goodroom-temperature compression properties and high work-hardening capacity at thestrain rate of1.0×10~(-4)s~(-1).
a) The ture yield strength, fracture strength, the fracture strain, the work-hardeningcapacity and the hardness of the NiAl are419MPa、1005MPa、21.6%、1.40and360HV, respectively.
b) The room-temprature compression properties were improved obviously with theaddition of5,10and15at.%Mo. The compression properties of the NiAl-15Moalloy are the best, and the ture yield strength, fracture strength, and the hardness are747MPa,1619MPa and621HV, respectively. While the ture fracture strain andthe work-hardening capacity are little, lower than those of the pure NiAl.
c) The addition of Cr can improve the compression properties of NiAl alloy.Among the NiAl-xCr alloys, the NiAl alloys with30at.%Cr has the best properties.The ture yield strength, fracture strength, the fracture strain, the work-hardeningcapacity and the hardness of the NiAl-30Cr alloy are809MPa,1909MPa,21.4%,1.35and667HV.390MPa,904MPa and307HV, respectively improve the trueyield strength, the fracture strength and the hardness. The ture fracture strain and the work-hardening capacity is as high as those of the pure NiAl alloy.
d) The compression properties of the NiAl-matrxi composite with5wt.%Nb_2C,NbB_2and NbC are the best among the different content and kind ceramicparticulates reinforced NiAl-matrix composites. The true yield strength, fracturestrength, and the hardness of the composite are653MPa,1497MPa and466HV,repectively. The fracture strain and the work-hardening capacity decreased lightly.
(4) It was found that the NiAl alloy, NiAl-Mo/Cr alloys have strain rate sensitivity.When the strain rate decrease from1.25×10~(-2)s~(-1)to1.0×10~(-4)s~(-1),
a) For NiAl, the fracture strain and the work-hardening capacity are improved by8.4%and0.62, respectively.The true yield strength and the fracture strength aredecreased by151MPa and15MPa, respectively.
b) For NiAl-30Cr alloys, the true fracture strength, fracture strain andwork-hardening capacity improved by118MPa,2.7%and0.65, especially thework-hardening capacity, which is improved by93%, while the yield strengthdecreased245MPa.
c) For NiAl-matrix composite with5wt.%Nb_2C, NbB_2and NbC, both of thestrength and the work-haedening capacity are improved by6.4%and0.46,respectively. The true fracture strength did not changed obviously, and the yieldstrength decreased149MPa.When the compression strain rate decreased from1.25×10~(-2)s~(-1)to5.0×10~(-4)s~(-1), thetrue yield strength, the frcacture strength, the fracture strain and thework-hardening capacity of the NiAl-15Mo alloy were improved by46MPa,250MPa,13.7%and0.2.
(5) The mechanism of the strengthening of the NiAl, NiAl-Mo/Cr, NiAl-matrixcomposite with Nb_2C, NbB_2and NbC was discussed.
a) The mechanism for NiAl, The NiAl fabricated by the high-temperaturecombustion reaction and hot press was refined, and the strength and the fracturestrain are improved. There were many dislocations distributed in the NiAl matrix,and the lattice of the NiAl distorted. The amount of dislactions increased during thecompression processing, from5.08×1011cm-2to5.92×1011cm-2, which canimprove the work-hardening capacity. Therefore, the mechanism for NiAl isfine-grained strengthening.
b) The mechanism of the NiAl-Mo/Cr alloys, Mo and Cr exsit in NiAl as threetypes. A proportion of Mo/Cr solutes to the NiAl, which leads to the latticedistorted. A proportion of Mo/Cr precitipitation in NiAl, and the size is about20-30 nm. As Mo and Cr is soft than NiAl, they exsit in NiAl as a soft phase. Anotherproportion of Cr/Mo distributed at the grain boundaries. The strengtheningmechanisms are fined-grain strengthening, solution strengthening and the secondphase strengthening.
c) The mechanism of the NiAl-matrix composite with5wt.%Nb_2C, NbB_2andNbC: The size of the ceramic paticulates in the grains is about1-2μm, while thesize of the ceramic particulates at the grain boundaries is about40μm. The amountof dislactions increased during the compression processing, from8.28×1011cm-2to1.20×1012cm-2, which can improve the work-hardening capacity. Therefore, themechanism for NiAl-matrix composite with Nb_2C, NbB_2and NbC is fine-grainedstrengthening and the second phase strengthening.
In summary, the effect of the addition of the ceramic and alloying elements on thecompression properties of NiAl was studied in this paper. It can be benifical to theimprovement for the compression properties of NiAl.
引文
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