Al-Ti-Si体系燃烧合成反应机制及产物
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摘要
本文主要研究了Al-Ti-Si该体系在DTA和TE两种不同条件下的反应机制和相转变顺序,并探讨了动力学因素(Al含量和反应物粒度等)对该体系SHS反应产物(种类、形貌、尺寸和数量等)的影响规律。
DTA条件下,Al的添加彻底改变了Ti-Si体系的反应路径。Al-Ti-Si体系的反应路径如下:Al_(l)+Ti_(s)+Si_(s)→(Al-Si)_(l)+Ti_(s)+Si_(s)→Ti(Al,Si)3_(s)+Si_(s)→Ti_5(Si,Al)_3_(s)+Al_(l)。此外,随Al含量的增加,Al-Ti-Si体系产物中Ti(Al,Si)3的含量显著增加,而Ti5(Si,Al)3的含量则明显降低。
TE条件下,与Ti-Si体系相比较,Al-Ti-Si体系的反应机制发生了明显的改变:首先是Al-Si液相的形成(预反应)和Ti(Al,Si)3中间相的形成(点火反应),并释放出大量的热;随后Ti(Al,Si)3和Si反应,生成Ti5(Si,Al)3和Al液(燃烧反应),该反应释放出的大量热导致领先相Ti(Al,Si)3以及残余的Ti和Si熔化并形成Al-Ti-Si三元液相;当熔体中的[Ti]和[Si]的浓度达到饱和时,反应析出Ti5(Si,Al)3。
随Al含量增加,Al-Ti-Si体系的燃烧温度逐渐降低,且主要产物的过渡顺序为:Ti5Si3→Ti5(Si,Al)3→Ti(Al,Si)3;Ti(Al,Si)3中Si原子的固溶量随Al含量的增加而显著增加,但Ti5(Si,Al)3中Al原子的固溶量主要取决于Al含量。此外,Al粉粒度对Al-Ti-Si体系反应产物相组成和形貌影响不大。Ti和Si粉粒度对产物相组成和尺寸影响不大;但对Ti5Si3的形貌有较大影响。与单相Ti5Si3或TiAl3相比,Ti5Si3-TiAl3复相组织晶粒细小,微裂纹减少。随设计Al2O3含量增加,热爆+热压合成的Ti5Si3-Al2O3复合材料的硬度值逐渐降低。
Structural intermetallic compounds, due to their high specific strength at elevated temperature, have been the subjects of numerous research works. In recent years, intermetallics of Ti–Si system have been the focus of significant research and development efforts. Among them, titanium silicide (Ti5Si3), has been considered as one of the most potential materials for high-temperature structure applications, in view of its high melting temperature (2130 oC), low density (4.32 g/cm3), capacity to retain high strength up to 1200 oC, and good oxidation and creep resistance at and below 850oC. However, Ti5Si3 has rather low toughness (~2.5MPam1/2) below the ductile-brittle transition temperature, and it often demonstrates brittle failure before plastic deformation, which severely limits its engineering application. Overall, the major challenge in applying Ti5Si3-based materials, like ceramic materials, is to reduce its brittleness or improve the room-temperature fracture toughness.
Despite a lot of efforts have been devoted and many routes are introduced to overcome the deficiencies of Ti5Si3, results are not as good as expected. During recent years, researchers have conducted a series of work which involves adding the third metal element to improve the combined properties of Ti5Si3. Theoretical calculation suggests that some alloying elements can reduce the CTE (Coefficients of Thermal Expansion) anisotropy of Ti5Si3 significantly, and hence reduce the microcracks in Ti5Si3. Experiment results show that the added alloying elements can serve as a diluent which decreases the reaction temperature in synthesizing Ti5Si3, and therefore may refine the Ti5Si3 grains. Furthermore, proper alloying elements can act as bonding agents after the reaction, which distributes in boundaries of grains, and thus improve the properties, such as strength and toughness, of Ti5Si3. In summery, the information above indicates that the addition of metal elements can enhance the fracture toughness of Ti5Si3, which inspired us to do more research on Me-Ti-Si system.
Since Al atoms might take place of either Ti or Si sites in Ti5Si3 lattices, and the remaining Al can distribute between the grains, it is expected that the addition of Al might improve the properties, especially the brittleness at room temperature or fracture toughness, of intermetallics Ti5Si3, and therefore establish considerable significance of the present study. Nevertheless, recent studies of Al-Ti-Si system mainly focused on certain aspects, such as technologies of fabrication and characterization of properties, while little research concentrated on reaction mechanisms, phase formation and evolution process of combustion synthesis in Al-Ti-Si system. As a consequence, in the present paper, we chose Al as an alloying element to fabricate Ti5Si3-basesd material via combustion synthesis, aimed to investigate the reaction mechanism of Al-Ti-Si system under DTA and TE modes. Particular attention was also paid to the effect of some dynamic factors, such as Al content and reactants size, on phase compositions and microstructures of reaction products of Al-Ti-Si system. It is expected that the present work could lay some theoretical and experimental foundation in the course of alloying of Ti5Si3. Besides, the present work also involves some research on Ti5Si3-TiAl3 and Ti5Si3-Al2O3 composites, mainly investigating the influence of designed volume fraction of TiAl3 and Al2O3 on the type and microstructures of the end products, respectively. Results of the present study are:
(1) The addition of Al changes the reaction path of Ti-Si system thoroughly under DTA condition. The raction path of Al-Ti-Si system can be described as following: Al(l)+Ti(s)+Si(s)→(Al-Si)(l)+Ti(s)+Si(s)→Ti(Al,Si)3(s)+Si(s)→Ti5(Si,Al)3(s)+Al(l). Moreover, the increase of Al addition increases the amount of Ti(Al,Si)3 considerably while decreases that of Ti5(Si,Al)3 remarkably.
(2) Compared with Ti-Si system, the reaction mechanism changes considerably under TE condition: first, Al and Si took reaction to form Al-Si liquid phase (pre-combustion reaction), and then Al-Si liquid reacted with Ti to form Ti(Al,Si)3 (ignition reaction), releasing some amount of heat, which triggered the reaction of Ti(Al,Si)3 and Si to form Ti5(Si,Al)3 (initial stage of combustion reaction), which released great amounts of heat, and thus, the prior intermediate phase Ti(Al,Si)3, remnant Si and Ti particles were likely to melt to form Al-Ti-Si ternary liquids (middle stage of combustion reaction). Once Ti and Si atoms in melts become sufficiently supersaturated, the precipitation of Ti5(Si,Al)3 grains occurred (end stage of combustion reaction). This process can be distinguished as a solution and precipitation mechanism. Moreover, with the Al addition increasing, the combustion temperature decrease significantly, and the dominated reaction in the initial stage of combustion changes from that between Ti(Al,Si)3 and Si to that between Al-Si liquid and Ti.
(3) With Al content increasing from 0 to 50 wt.%, the maximum combustion temperature of Al-Ti-Si system decreased, and the microstructure evolution process can be concluded through a transition chain as follows: Ti5Si3→Ti5(Si,Al)3→Ti(Al,Si)3. Furthermore, the solubility of Si in TiAl3 increased significantly with increasing Al addition, while that of Al in Ti5Si3 mainly depended on the Al content. As Al addition increased from 0 to 25wt.%, the size of Ti5Si3 particle decreased from ~20μm to ~8μm, also the morphology changed from irregular polygon to cobblestone-like shape with smooth surface. Furthermore, the size of reactants didn’t cause any significant influence on the type and size of reaction products, but the size of Ti and Si particles impacted the morphology of the products to some extent, eg. Ti5Si3 grains gradually changes from tuber or plates -shape to cobblestone shape.
(4) Compared with the the microstructure of single-phase Ti5Si3 or TiAl3, that of Ti5Si3-TiAl3 dual phases refined apparently; and the microcracks reduced gradually as the designed TiAl3 volume fraction increasesd. When the designed Al2O3 volume fraction increased over the range of 10-20 vol.%, the actual Al2O3 content in Ti5Si3-Al2O3 composites increased, and the size of Ti5Si3 particles decreased significantly while its morphologies changed remarkably. With the designed Al2O3 volume fraction increased from 10 to 20 vol.%, the hardness values, of Ti5Si3-Al2O3 composites syntheised by TE combined with pressure, decreased gradually.
DTA条件下,Al的添加彻底改变了Ti-Si体系的反应路径。Al-Ti-Si体系的反应路径如下:Al_(l)+Ti_(s)+Si_(s)→(Al-Si)_(l)+Ti_(s)+Si_(s)→Ti(Al,Si)3_(s)+Si_(s)→Ti_5(Si,Al)_3_(s)+Al_(l)。此外,随Al含量的增加,Al-Ti-Si体系产物中Ti(Al,Si)3的含量显著增加,而Ti5(Si,Al)3的含量则明显降低。
TE条件下,与Ti-Si体系相比较,Al-Ti-Si体系的反应机制发生了明显的改变:首先是Al-Si液相的形成(预反应)和Ti(Al,Si)3中间相的形成(点火反应),并释放出大量的热;随后Ti(Al,Si)3和Si反应,生成Ti5(Si,Al)3和Al液(燃烧反应),该反应释放出的大量热导致领先相Ti(Al,Si)3以及残余的Ti和Si熔化并形成Al-Ti-Si三元液相;当熔体中的[Ti]和[Si]的浓度达到饱和时,反应析出Ti5(Si,Al)3。
随Al含量增加,Al-Ti-Si体系的燃烧温度逐渐降低,且主要产物的过渡顺序为:Ti5Si3→Ti5(Si,Al)3→Ti(Al,Si)3;Ti(Al,Si)3中Si原子的固溶量随Al含量的增加而显著增加,但Ti5(Si,Al)3中Al原子的固溶量主要取决于Al含量。此外,Al粉粒度对Al-Ti-Si体系反应产物相组成和形貌影响不大。Ti和Si粉粒度对产物相组成和尺寸影响不大;但对Ti5Si3的形貌有较大影响。与单相Ti5Si3或TiAl3相比,Ti5Si3-TiAl3复相组织晶粒细小,微裂纹减少。随设计Al2O3含量增加,热爆+热压合成的Ti5Si3-Al2O3复合材料的硬度值逐渐降低。
Structural intermetallic compounds, due to their high specific strength at elevated temperature, have been the subjects of numerous research works. In recent years, intermetallics of Ti–Si system have been the focus of significant research and development efforts. Among them, titanium silicide (Ti5Si3), has been considered as one of the most potential materials for high-temperature structure applications, in view of its high melting temperature (2130 oC), low density (4.32 g/cm3), capacity to retain high strength up to 1200 oC, and good oxidation and creep resistance at and below 850oC. However, Ti5Si3 has rather low toughness (~2.5MPam1/2) below the ductile-brittle transition temperature, and it often demonstrates brittle failure before plastic deformation, which severely limits its engineering application. Overall, the major challenge in applying Ti5Si3-based materials, like ceramic materials, is to reduce its brittleness or improve the room-temperature fracture toughness.
Despite a lot of efforts have been devoted and many routes are introduced to overcome the deficiencies of Ti5Si3, results are not as good as expected. During recent years, researchers have conducted a series of work which involves adding the third metal element to improve the combined properties of Ti5Si3. Theoretical calculation suggests that some alloying elements can reduce the CTE (Coefficients of Thermal Expansion) anisotropy of Ti5Si3 significantly, and hence reduce the microcracks in Ti5Si3. Experiment results show that the added alloying elements can serve as a diluent which decreases the reaction temperature in synthesizing Ti5Si3, and therefore may refine the Ti5Si3 grains. Furthermore, proper alloying elements can act as bonding agents after the reaction, which distributes in boundaries of grains, and thus improve the properties, such as strength and toughness, of Ti5Si3. In summery, the information above indicates that the addition of metal elements can enhance the fracture toughness of Ti5Si3, which inspired us to do more research on Me-Ti-Si system.
Since Al atoms might take place of either Ti or Si sites in Ti5Si3 lattices, and the remaining Al can distribute between the grains, it is expected that the addition of Al might improve the properties, especially the brittleness at room temperature or fracture toughness, of intermetallics Ti5Si3, and therefore establish considerable significance of the present study. Nevertheless, recent studies of Al-Ti-Si system mainly focused on certain aspects, such as technologies of fabrication and characterization of properties, while little research concentrated on reaction mechanisms, phase formation and evolution process of combustion synthesis in Al-Ti-Si system. As a consequence, in the present paper, we chose Al as an alloying element to fabricate Ti5Si3-basesd material via combustion synthesis, aimed to investigate the reaction mechanism of Al-Ti-Si system under DTA and TE modes. Particular attention was also paid to the effect of some dynamic factors, such as Al content and reactants size, on phase compositions and microstructures of reaction products of Al-Ti-Si system. It is expected that the present work could lay some theoretical and experimental foundation in the course of alloying of Ti5Si3. Besides, the present work also involves some research on Ti5Si3-TiAl3 and Ti5Si3-Al2O3 composites, mainly investigating the influence of designed volume fraction of TiAl3 and Al2O3 on the type and microstructures of the end products, respectively. Results of the present study are:
(1) The addition of Al changes the reaction path of Ti-Si system thoroughly under DTA condition. The raction path of Al-Ti-Si system can be described as following: Al(l)+Ti(s)+Si(s)→(Al-Si)(l)+Ti(s)+Si(s)→Ti(Al,Si)3(s)+Si(s)→Ti5(Si,Al)3(s)+Al(l). Moreover, the increase of Al addition increases the amount of Ti(Al,Si)3 considerably while decreases that of Ti5(Si,Al)3 remarkably.
(2) Compared with Ti-Si system, the reaction mechanism changes considerably under TE condition: first, Al and Si took reaction to form Al-Si liquid phase (pre-combustion reaction), and then Al-Si liquid reacted with Ti to form Ti(Al,Si)3 (ignition reaction), releasing some amount of heat, which triggered the reaction of Ti(Al,Si)3 and Si to form Ti5(Si,Al)3 (initial stage of combustion reaction), which released great amounts of heat, and thus, the prior intermediate phase Ti(Al,Si)3, remnant Si and Ti particles were likely to melt to form Al-Ti-Si ternary liquids (middle stage of combustion reaction). Once Ti and Si atoms in melts become sufficiently supersaturated, the precipitation of Ti5(Si,Al)3 grains occurred (end stage of combustion reaction). This process can be distinguished as a solution and precipitation mechanism. Moreover, with the Al addition increasing, the combustion temperature decrease significantly, and the dominated reaction in the initial stage of combustion changes from that between Ti(Al,Si)3 and Si to that between Al-Si liquid and Ti.
(3) With Al content increasing from 0 to 50 wt.%, the maximum combustion temperature of Al-Ti-Si system decreased, and the microstructure evolution process can be concluded through a transition chain as follows: Ti5Si3→Ti5(Si,Al)3→Ti(Al,Si)3. Furthermore, the solubility of Si in TiAl3 increased significantly with increasing Al addition, while that of Al in Ti5Si3 mainly depended on the Al content. As Al addition increased from 0 to 25wt.%, the size of Ti5Si3 particle decreased from ~20μm to ~8μm, also the morphology changed from irregular polygon to cobblestone-like shape with smooth surface. Furthermore, the size of reactants didn’t cause any significant influence on the type and size of reaction products, but the size of Ti and Si particles impacted the morphology of the products to some extent, eg. Ti5Si3 grains gradually changes from tuber or plates -shape to cobblestone shape.
(4) Compared with the the microstructure of single-phase Ti5Si3 or TiAl3, that of Ti5Si3-TiAl3 dual phases refined apparently; and the microcracks reduced gradually as the designed TiAl3 volume fraction increasesd. When the designed Al2O3 volume fraction increased over the range of 10-20 vol.%, the actual Al2O3 content in Ti5Si3-Al2O3 composites increased, and the size of Ti5Si3 particles decreased significantly while its morphologies changed remarkably. With the designed Al2O3 volume fraction increased from 10 to 20 vol.%, the hardness values, of Ti5Si3-Al2O3 composites syntheised by TE combined with pressure, decreased gradually.
引文
[1] MITRA R. Microstructure and mechanical behavior of reaction hot pressed Titanium silicide and Titanium silicide-based alloys and composites [J]. Metall. Mater. Trans., 1998,A29:1629-1648.
[2] ROSENKRANZ R,FROMMEYER G,Smarsly W. Microstructures and properties of high melting point intermetallics Ti5Si3 and TiSi2 composites [J]. Mater. Sci. Eng., 1992, A152: 288-294.
[3] PARK K L,HWANG S K. Synthesis of Ti5Si3-Nb-C by electro-pressure sintering [J].Scr. Mater., 2001, 44: 9-16.
[4] RILEY D P, OLIVER C P,KISI E H,In-situ neutron diffraction of titanium silicide, Ti5Si3, during self-propagating high-temperature synthesis [J]. Intermetallics, 2006, 14: 33-38.
[5] Li J L, J D L, et al. Microstructure and mechanical properties of in situ produced Ti5Si3/TiC nanocomposites [J]. J. Euro. Ceram. Soc., 2002, 22: 551-558.
[6] ZHANG L T, WU, J S. Ti5Si3 and Ti5Si3-based alloys: alloying behavior, microstructure and mechanical property evaluation [J]. Acta. Mater., 1998, 46: 3535-3546.
[7] KOCH C C. Intermetallic matrix composites prepared by mechanical alloying - a review [J]. Materials Science and Engineering A, 1998, 244: 39-48.
[8] SHILPA A, ERIC J C, SERGEI Z, ROBERT K, CLIFFORD M. The heat capacities of titanium silicides Ti5Si3, TiSi and TiSi2 [J]. J. Alloy. Compd.,2001, 314: 99-102.
[9] WILLIAMS J J, YE Y Y. Theoretical calculations and experimental measurements of the structure of Ti5Si3 with interstitial additions [J]. Intermetallics, 2000, 8: 937-943.
[10] SCHNEIBEL J H, RAWN C J. Thermal expansion anisotropy of ternary titanium silicides based on Ti5Si3 [J]. Acta. Mater., 2004, 52: 3843-3848.
[11] SHAN D M, BERCZIK D, ANTON D L, HECHT R. Appraisal of other silicides as structureal materials [J]. Mater. Sci. Eng., 1992, A155: 45-57.
[12] PARK K J, HONG J K, HWANG S K. Effect of Cu addition on consolidating Ti5Si3 by the elemental powder-metallurgical Method [J]. Met. Trans., 1997, 28A: 223-228.
[13] PARK H C, KIM M S, HWANG S K, Consolidation of Ti5Si3-Cu alloy by hot deformation of elemental powder mixtures [J]. Scr. Mater., 1998, 39: 1585-1591.
[14] YEN B K, AIZAWA T, KIHARA J. Reaction synthesis of titanium silicides via self-propagating reaction kinetics [J]. J. Am. Ceram. Soc., 1998, 81: 1953-1956.
[15] COUNIHAN P J, CRAWFORD A, THADHANI N N. Influence of dynamic densification on nanostructure formation in Ti5Si3 intermetallic alloy and its bulk properties [J].Mater. Sci. Eng. A, 1999, A267: 26.
[16] CALKA A, RADLINSKI A P. Formation of Titanium sillides by michanical alloying [J]. J. Mater. Sci. Lett. 1991, 10:734-737.
[17] MOORE J J, FENG H J. Combustion synthesis of advanced materials: Part I. Reaction parameters [J]. Progress in Materials Science, 1995, 39: 243-273.
[18] Cao G, OrrùR. Self-propagating reactions for environmental protection: state of the art and future directions [J]. Chem. Eng. J., 2002, 87: 239-249.
[19] BISWAS A, ROY S K, GURUMURTHY K R, PRABHUC N, BANERJEE S. A study of self-propagating high-temperature synthesis of NiAl in thermal explosion mode [J]. Acta Mater. 2002, 50:757-773.
[20] TAMBURINI U A, MAGLIA F, SPINOLO G, DOPPIU S, MONAGHEDDU M, COCCO G. Self-propgating reacions in the Ti-Si systems [J]. J. Mater. Synth. Process, 2000, 8: 377-383.
[21] KACHELMYER C R, KHOMENKO I O, ROGACHEV A S, VARMA A. A time-resolved x-ray diffraction study of Ti5Si3 product formation of during combustion synthesis [J], J. Mater. Res., 1997, 12: 3230–3240.
[22] ROGACHEV A S, SHUGAEV V A, KHOMENKO I, VARMA A, KACHELMYER C R. On the mechanism of structure formation during combustion synthesis of Titanium sillides [J]. Combust. Sci. Tech., 1995, 109: 53-70.
[23] GENNARI S, TAMBURINI U A, MAGLIA F, SPINOLO G, MUNIR Z A. A new approach to the modeling of SHS reactions: Combustion synthesis of transition metal aluminides [J].Acta. Mater., 2006, 54: 2343-2351.
[24] TRAMBUKLS J, MUNIR Z A. Effect of partical dispersion on the mechanism of combustion synthesis of titanlum silicide [J]. J. Am. Ceram. Soc., 1990, 73: 1240-1245.
[25]殷声.燃烧合成[M].北京:冶金工业出版社,2004.
[26] MERZHANOV A G. Self-propagating high-temperature synthesis: Twenty years of search and findings, Combustion and Plasma Synthesis of High-temperature materials [M], edited by Z.A. Munir and J.B. Holt, VCH, Weinheim, New York, 1990; 1.
[27] YEH C L, CHEN W H, HSU C.C. Formation of titanium silicides Ti5Si3 and TiSi2 by self-propagating combustion synthesis [J]. J. Alloy. Compd. 2007, 432: 90-95.
[28] YEH C L, CHEN W H, HSU C C. An experimental study on Ti5Si3 Formation by combustion synthesis in self-propagating mode [J]. J. Alloy. Compd., 2005, 395: 53-58.
[29] WANG C, WANG Y, XIA Y, DONG C. Laser-induced self-propagating high-temperature synthesis of amorphous- and quasycrystal-containing composite materials [J]. Journal of Non-crystalline Solids, 2004; 334-335: 513.
[30] Chen H C, Lasalvia J C, Nesterenko V F, Meyers M A. Shear localization and chemical reaction in high deformation of Ti-Si powder mixtures [J]. Acta. Mater., 1998, 46: 3033-3046.
[31] DEEVI S C, THAHANI N N. Reaction synthesis of high-temperature silicides [J]. Mater. Sci. Eng., 1995, A192/193: 604-611.
[32] KANG B Y, RYOO H S, HWANG W, HWANG S K, KIM S.W. Explosion synthesis of Ti5Si3-Cu intermetallic compound [J]. Mater. Sci. Eng. 1999, A270330-338.
[33] Das K, Gupta Y M, Bandyopadhyay A. Titanium silicide (Ti5Si3) synthesis under shock loading [J]. Mater. Sci. Eng., 2006, A426: 147-156.
[34] KRUEGER B R, MUTZ A H, VREELAND JR. T. Shock-induced and self-propagating high-temperatures synthesis reactions in two powder mixtures: 5:3 atomic ratio Ti/Si and 1:1 atomic ratio Ni/Si [J]. Meta. Tran., 1992, 23A: 55-58.
[35] THADHANI N N, GRAHAM R A, ROYAL T, DUNBAR E, ANDERSON M U, HOLMAN G T. Shock-induced chemical reactions in titanium-silicon powder mixtures of different morphologies: Time-resolved pressure measurements and materials analysis [J]. J. Appl. Phys., 1997, 82: 1113-1128.
[36] THADHANI N.N. Shock-induced and shock-assisted solid-state chemical reactions in powder mixture [J]. J. Appl. Phys., 1994, 76: 2129-2138.
[37] THADHANI N N, Namjoshi S, Counihan P J, Crawford A. shock-assisted synthesis of Ti5Si3 intermetallic compound [J]. J. Mater. Process. Technol., 1999, 85: 74-78.
[38] REUSS S, VEHOFF H. Temperature dependence of the fracture toughness of single phase and two phase intermetallics [J]. Scripta Metal. Mater., 1990; 24: 1021.
[39] GUAN Q L, WANG H Y, LI S L, ZHANG W N, JIANG Q C. Effect of Fe addition on self-propagating high-temperature synthesis of Ti5Si3 in Fe-Ti-Si system [J]. J. Alloys Compd., 2007, 456: 79-84.
[40]关庆铃. Fe添加对Ti-Si系燃烧合成反应路径及行为的影响[D].长春:吉林大学材料学院,2009.
[41] WANG H Y, LüSJ, ZHA M, LI S T, LIU C, JIANG Q C. Influence of Cu addition on the self-propagating high-temperature synthesis of Ti5Si3 in Cu-Ti-Si system [J]. Materials Chemistry and Physical, 2008, 111: 463-468.
[42] WILLIAMS J J, KRAMER M J, AKINC M. Thermal expansion of Ti5Si3 with Ge, B, C, N, or O additions [J]. J. Mater. Res., 2000, 15: 1780-1785.
[43] WILLIAMS J J, KRAMER M J, AKINC M, MALIK S K. Effects of interstitial additions on the structure of Ti5Si3 [J]. J. Mater. Res., 2000; 15: 1773.
[44] SAMBASIVAN S A, PETUSKEY W T. Phase Chemistry in the Ti-Si-N system: Thermochemical Review with Phase Stability Diagrams [J]. J. Mater. Res., 1994; 9: 2362.
[45] ZHANG H B, ZHOU Y C, BAO Y W, LI M S, WANG J Y. Intermediate phases in synthesis of Ti3SiC2 and Ti3Si(Al)C2 solid solutions from elemental powders [J]. J. Eur. Ceram. Soc., 2006, 26: 2373-2380.
[46] TANG Z H, WILLIAMS J J, THOM A J, AKINC M. High temperature oxidation behavior of Ti5Si3-based intermetallics [J]. Intermetallics, 2008, 16: 1118-1124.
[47] SCHNEIBEL J H, RAWN C J, PAYZANT E A, FU C L. Controlling the thermal expansion anisotropy of Mo5Si3 and Ti5Si3 silicides [J]. Intermetallics, 2004, 12: 845-850.
[48] IKARASHI Y, ISHIZAKI K, NAGAI T, HASHIZUKA Y, KONDO Y. Reduction of thermal expansion anisotropy for intermetallie suicides of 16H crystal structure [J]. Intermetallics 1996, 4:S141.
[49] WARD-CLOSE C M, MINOR R, DOORBAR P J. Intermetallic-matrix composites - a review [J]. Intermetallics [J]. 1996, 4: 217-229.
[50] SHON I J, MUNIR Z A. Electric field-activated combustion synthesis of Ti5Si3-Nb and Ti5Si3-ZrO2 composites [J]. J. Mater. Sci., 1997, 32: 5805-5810.
[51] SHON I J, KIM H C, RHO D H, MUNIR Z A. Simultaneous synthesis and densification of Ti5Si3 and Ti5Si3-20 vol% ZrO2 composites by field-activated and pressure-assisted combustion [J]. Mater. Sci. Eng., 1999, A269: 129-135.
[52]李建林,江东亮,谭寿洪.原位生成TiC/Ti5Si3纳米复合材料的显微结构研究[J].无机材料学报, 2000, 15: 336-340.
[53]李建林,江东亮,谭寿洪.原位生成TiC/Ti5Si3纳米复合材料的显微结构[J].金属学报, 1999, 35: 893-896.
[54] WANG L, JIANG W, QIN C, CHEN L. Effect of starting SiC particle size on in situ fabrication of Ti5Si3/TiC composites [J]. Mater. Sci. Eng., 2006, A425: 219-224.
[55] LIN ZJ, ZHOU M J, ZHOU Y C, LI M S, WANG J Y. Microstructural relationships between compounds in the Ti-Si-C system [J]. Scripta Mater., 2006, 55: 445-448.
[56] YEH C L, TENG G S. Use of si3n4 as a reactant in preparation of tin-ti5si3 composites by solid-state shs reactions [J]. J. Alloys. Comp., 2007, 429: 126-132.
[57] ALMAN DE. Reactive sintering of TiAl-Ti5Si3 in situ composites [J]. Intermetallics, 2005, 13: 572-579.
[58] KLASSEN T, SURYANARAYANA C, BORMANN R. Low-temperature superplasticity in ultrafine-grained Ti5Si3-TiAl composites [J]. Script Mater., 2008, 59: 455-458.
[59] RAO K P, ZHOU J B. Charecterization of mechanically alloyed Ti-Al-Si powder blends and their subsequent thermal stability [J]. Mater. Sci. Eng., 2002, A338: 282-294.
[60] RAO K P, ZHOU J B. Charecterization and mechanical properties of in situ synthesized Ti5Si3 /TiAl composites [J]. Mater. Sci. Eng., 2003, A356: 208-218.
[61] GUAN Z Q, PFULLMANN T, OEHRING M, BORMANN R. Phase formation during ball milling and subsequent thermal decomposition of Ti-Al-Si powder blends [J]. J. Alloy. Compd., 1997, 252: 245-251.
[62] YEH C L, LI R F. Formation of TiAl-Ti5Si3 and TiAl -Al2O3 in situ composites by combustion synthesis [J]. Intermetallics, 2008, 16: 64-70.
[63] VOJTECH D, NOVAK M, NOVAK P, LEJCEK P, KOPECEK J. Unidirectional crystallization and high-temperature oxidation of in situ Ti3(Al,Si)-Ti5(Si,Al)3 composite [J]. Mater. Sci. Eng., 2008, A489: 1-10.
[64]李世龙. Ni掺杂下Ti5Si3的燃烧合成反应路径及电子结构计算[D].长春:吉林大学材料学院,2009.
[65] LIANG Y J, CHEN Y C. Data handbook of Mineral Thermodynamics [M]. edited by Northeastern Press, 1993 (in China).
[66] BRAIN I. Thermochemical Data of Pure Substance [M]. 3rd ed., WILEY-VCH Verlag GmbH: 1995.
[67] HOLT J, MUNIR Z A. Combustion synthesis of titanium carbide: theory and experiment [J]. J. Mater. Sci., 1986, 21: 251.
[68] SENKOV O N, Cavusoglu M, Froes F H. Synthesis and characterization of a TiAl/Ti5Si3 composite with a submicrocrystalline structure [J]. Mater. Sci. Eng. 2001, A300: 85-93.
[69] DU Y J, RAO K P, CHUNG J C Y, HAN X D. Phase transitions in reactive formation of Ti5Si3/TiAl in situ composites [J]. Metall. Mater. Trans. 2000, A31: 763-771.
[70] CUPTA S P. Intermetallic compounds in diffusion couples of Ti with an Al-Si eutectic alloy [J].Mater. Charact. 2003, 493: 21-330.
[71] CHRYSANTHOU A, OPOKU E K. HAN L. An investigation of the self-propagating high-temperature synthesis of Ti(Si,Al)2 [J]. J. Mater. Sci. 2005, 40: 2579-2581.
[72] MASSALSKI T B. ET AL. Binary Alloy Phase Diagrams [J]. 2nd ed., USA: ASM international Materials Park, OH, 1990.
[73] FU M. A study of micropyretic reactions in the Mo-Si-Al ternary system [J]. J. Mater.Res.1997, 12: 1481-1491.
[74] WANG T, ZHANG J. Thermoanalytical and metallographical investigations on the synthesis of TiAl3 from elementary powders [J]. Mater. Chem.Phys.2006, 99: 20-25.
[75] NASSAJ E T, KOBASHI M. CHOH T. Fabrication and analysis of in situ formed boride/Al composites by reactive spontaneous infiltration [J]. Script Mater. 1997, 37: 605-614.
[76] BRINKMAN H J, DUSZCZYK J, KATGERMAN L. In-situ formation of TiB2 in a P/M aluminum matrix [J]. Scr. Mater. 1997, 37: 293-3297.
[77] WANG H Y, JIANG Q C, LI X L, WANG J G.In situ synthesis of TiC/Mg composites in molten magnesium [J]. Script Mater. 2003,48: 1349–1354.
[78] LEE S H, LEE J H, LEE Y H, SHIN D H, KIM Y S. Effect of heating rate on the combustion synthesis of intermetallics [J]. Mater. Sci. Eng. 2000, A281: 275–285.
[79] BISWAS A, ROY S K, GURUMURTHY K R, PRABHU N, BANERJEE S. A study of self-propagating high-temperature synthesis of NiAl in thermal explosion mode [J]. Acta Mater. 2002, 50:757-773.
[80] YI H C, PETRIC A, MOORE J J. Effect of heating rate on the combustion synthesis of Ti-Al intermetallic compounds [J]. J. Mater. Sci. 1992, 27: 6797-6806.
[81] Powder Diffraction File Card No. 29–1362 for Ti5Si3 and 37-1449 for TiAl3 (CD ROM), International Center for Diffraction Data (ICDD) [M]. Newtown Square, PA.
[82] VEHOFF H, REUSS S, VOGT W, SPECHT P, Structure Intermetallics 1993, 657-663.
[83] WU J S, BEAVEN P A, WAGNER R. The Ti3(AI,Si)+Ti5(Si,AI)3 eutectic reaction in the Ti-A1-Si system [J]. Scr. Metall, 1990,24:207-212.
[84] J. WU, G. QIU AND L. ZHANG, Theβ-Ti(Al,Si)+Ti5(Si,Al)3 eutectic reaction in the Ti-Al-Si ternary system [J]. Scr Met Mater. 1994, 30: 213-218.
[85] BRUKL C, NOWOTNY H, SCHOB O, BENESOVSKY F. The crystal structure of TiSi, Ti(Al,Si)2 and Mo(Al,Si)2. [J]. Chem. Monthly, German: 1961, 92: 781-788.
[86] RAMAN A, SCHUBERT K. On the constitution of some alloy series related to TiAl3: II. Investigation on some systems Ti-Al-Si and T4..6 [J]. Z Metkd: 1965; 56: 44-52.
[87] YI H C, MOORE J J. Review of self-propagating high temperature (combustion) synthesis (SHS) of powder-compacted materials [J]. J. Mater.sci. 1990, 25: 1159-1168.
[88] MILMAN Y V, MIRACLE B, CHUGUNOVA S I, VOSKOBOINIK I V, KORZHOVA N P, LEGKAYA T N, PODREZOV Y N. Mechanical behavior of Al3Ti intermetallic and L12 phases on its basis [J]. Intermetallics, 2001, 9: 839.
[89] THOM A J, MEYER M K, KIM Y, AKINC M, RAVI V A, SRIVATSAN T S, MOORE J J, Processing
[2] ROSENKRANZ R,FROMMEYER G,Smarsly W. Microstructures and properties of high melting point intermetallics Ti5Si3 and TiSi2 composites [J]. Mater. Sci. Eng., 1992, A152: 288-294.
[3] PARK K L,HWANG S K. Synthesis of Ti5Si3-Nb-C by electro-pressure sintering [J].Scr. Mater., 2001, 44: 9-16.
[4] RILEY D P, OLIVER C P,KISI E H,In-situ neutron diffraction of titanium silicide, Ti5Si3, during self-propagating high-temperature synthesis [J]. Intermetallics, 2006, 14: 33-38.
[5] Li J L, J D L, et al. Microstructure and mechanical properties of in situ produced Ti5Si3/TiC nanocomposites [J]. J. Euro. Ceram. Soc., 2002, 22: 551-558.
[6] ZHANG L T, WU, J S. Ti5Si3 and Ti5Si3-based alloys: alloying behavior, microstructure and mechanical property evaluation [J]. Acta. Mater., 1998, 46: 3535-3546.
[7] KOCH C C. Intermetallic matrix composites prepared by mechanical alloying - a review [J]. Materials Science and Engineering A, 1998, 244: 39-48.
[8] SHILPA A, ERIC J C, SERGEI Z, ROBERT K, CLIFFORD M. The heat capacities of titanium silicides Ti5Si3, TiSi and TiSi2 [J]. J. Alloy. Compd.,2001, 314: 99-102.
[9] WILLIAMS J J, YE Y Y. Theoretical calculations and experimental measurements of the structure of Ti5Si3 with interstitial additions [J]. Intermetallics, 2000, 8: 937-943.
[10] SCHNEIBEL J H, RAWN C J. Thermal expansion anisotropy of ternary titanium silicides based on Ti5Si3 [J]. Acta. Mater., 2004, 52: 3843-3848.
[11] SHAN D M, BERCZIK D, ANTON D L, HECHT R. Appraisal of other silicides as structureal materials [J]. Mater. Sci. Eng., 1992, A155: 45-57.
[12] PARK K J, HONG J K, HWANG S K. Effect of Cu addition on consolidating Ti5Si3 by the elemental powder-metallurgical Method [J]. Met. Trans., 1997, 28A: 223-228.
[13] PARK H C, KIM M S, HWANG S K, Consolidation of Ti5Si3-Cu alloy by hot deformation of elemental powder mixtures [J]. Scr. Mater., 1998, 39: 1585-1591.
[14] YEN B K, AIZAWA T, KIHARA J. Reaction synthesis of titanium silicides via self-propagating reaction kinetics [J]. J. Am. Ceram. Soc., 1998, 81: 1953-1956.
[15] COUNIHAN P J, CRAWFORD A, THADHANI N N. Influence of dynamic densification on nanostructure formation in Ti5Si3 intermetallic alloy and its bulk properties [J].Mater. Sci. Eng. A, 1999, A267: 26.
[16] CALKA A, RADLINSKI A P. Formation of Titanium sillides by michanical alloying [J]. J. Mater. Sci. Lett. 1991, 10:734-737.
[17] MOORE J J, FENG H J. Combustion synthesis of advanced materials: Part I. Reaction parameters [J]. Progress in Materials Science, 1995, 39: 243-273.
[18] Cao G, OrrùR. Self-propagating reactions for environmental protection: state of the art and future directions [J]. Chem. Eng. J., 2002, 87: 239-249.
[19] BISWAS A, ROY S K, GURUMURTHY K R, PRABHUC N, BANERJEE S. A study of self-propagating high-temperature synthesis of NiAl in thermal explosion mode [J]. Acta Mater. 2002, 50:757-773.
[20] TAMBURINI U A, MAGLIA F, SPINOLO G, DOPPIU S, MONAGHEDDU M, COCCO G. Self-propgating reacions in the Ti-Si systems [J]. J. Mater. Synth. Process, 2000, 8: 377-383.
[21] KACHELMYER C R, KHOMENKO I O, ROGACHEV A S, VARMA A. A time-resolved x-ray diffraction study of Ti5Si3 product formation of during combustion synthesis [J], J. Mater. Res., 1997, 12: 3230–3240.
[22] ROGACHEV A S, SHUGAEV V A, KHOMENKO I, VARMA A, KACHELMYER C R. On the mechanism of structure formation during combustion synthesis of Titanium sillides [J]. Combust. Sci. Tech., 1995, 109: 53-70.
[23] GENNARI S, TAMBURINI U A, MAGLIA F, SPINOLO G, MUNIR Z A. A new approach to the modeling of SHS reactions: Combustion synthesis of transition metal aluminides [J].Acta. Mater., 2006, 54: 2343-2351.
[24] TRAMBUKLS J, MUNIR Z A. Effect of partical dispersion on the mechanism of combustion synthesis of titanlum silicide [J]. J. Am. Ceram. Soc., 1990, 73: 1240-1245.
[25]殷声.燃烧合成[M].北京:冶金工业出版社,2004.
[26] MERZHANOV A G. Self-propagating high-temperature synthesis: Twenty years of search and findings, Combustion and Plasma Synthesis of High-temperature materials [M], edited by Z.A. Munir and J.B. Holt, VCH, Weinheim, New York, 1990; 1.
[27] YEH C L, CHEN W H, HSU C.C. Formation of titanium silicides Ti5Si3 and TiSi2 by self-propagating combustion synthesis [J]. J. Alloy. Compd. 2007, 432: 90-95.
[28] YEH C L, CHEN W H, HSU C C. An experimental study on Ti5Si3 Formation by combustion synthesis in self-propagating mode [J]. J. Alloy. Compd., 2005, 395: 53-58.
[29] WANG C, WANG Y, XIA Y, DONG C. Laser-induced self-propagating high-temperature synthesis of amorphous- and quasycrystal-containing composite materials [J]. Journal of Non-crystalline Solids, 2004; 334-335: 513.
[30] Chen H C, Lasalvia J C, Nesterenko V F, Meyers M A. Shear localization and chemical reaction in high deformation of Ti-Si powder mixtures [J]. Acta. Mater., 1998, 46: 3033-3046.
[31] DEEVI S C, THAHANI N N. Reaction synthesis of high-temperature silicides [J]. Mater. Sci. Eng., 1995, A192/193: 604-611.
[32] KANG B Y, RYOO H S, HWANG W, HWANG S K, KIM S.W. Explosion synthesis of Ti5Si3-Cu intermetallic compound [J]. Mater. Sci. Eng. 1999, A270330-338.
[33] Das K, Gupta Y M, Bandyopadhyay A. Titanium silicide (Ti5Si3) synthesis under shock loading [J]. Mater. Sci. Eng., 2006, A426: 147-156.
[34] KRUEGER B R, MUTZ A H, VREELAND JR. T. Shock-induced and self-propagating high-temperatures synthesis reactions in two powder mixtures: 5:3 atomic ratio Ti/Si and 1:1 atomic ratio Ni/Si [J]. Meta. Tran., 1992, 23A: 55-58.
[35] THADHANI N N, GRAHAM R A, ROYAL T, DUNBAR E, ANDERSON M U, HOLMAN G T. Shock-induced chemical reactions in titanium-silicon powder mixtures of different morphologies: Time-resolved pressure measurements and materials analysis [J]. J. Appl. Phys., 1997, 82: 1113-1128.
[36] THADHANI N.N. Shock-induced and shock-assisted solid-state chemical reactions in powder mixture [J]. J. Appl. Phys., 1994, 76: 2129-2138.
[37] THADHANI N N, Namjoshi S, Counihan P J, Crawford A. shock-assisted synthesis of Ti5Si3 intermetallic compound [J]. J. Mater. Process. Technol., 1999, 85: 74-78.
[38] REUSS S, VEHOFF H. Temperature dependence of the fracture toughness of single phase and two phase intermetallics [J]. Scripta Metal. Mater., 1990; 24: 1021.
[39] GUAN Q L, WANG H Y, LI S L, ZHANG W N, JIANG Q C. Effect of Fe addition on self-propagating high-temperature synthesis of Ti5Si3 in Fe-Ti-Si system [J]. J. Alloys Compd., 2007, 456: 79-84.
[40]关庆铃. Fe添加对Ti-Si系燃烧合成反应路径及行为的影响[D].长春:吉林大学材料学院,2009.
[41] WANG H Y, LüSJ, ZHA M, LI S T, LIU C, JIANG Q C. Influence of Cu addition on the self-propagating high-temperature synthesis of Ti5Si3 in Cu-Ti-Si system [J]. Materials Chemistry and Physical, 2008, 111: 463-468.
[42] WILLIAMS J J, KRAMER M J, AKINC M. Thermal expansion of Ti5Si3 with Ge, B, C, N, or O additions [J]. J. Mater. Res., 2000, 15: 1780-1785.
[43] WILLIAMS J J, KRAMER M J, AKINC M, MALIK S K. Effects of interstitial additions on the structure of Ti5Si3 [J]. J. Mater. Res., 2000; 15: 1773.
[44] SAMBASIVAN S A, PETUSKEY W T. Phase Chemistry in the Ti-Si-N system: Thermochemical Review with Phase Stability Diagrams [J]. J. Mater. Res., 1994; 9: 2362.
[45] ZHANG H B, ZHOU Y C, BAO Y W, LI M S, WANG J Y. Intermediate phases in synthesis of Ti3SiC2 and Ti3Si(Al)C2 solid solutions from elemental powders [J]. J. Eur. Ceram. Soc., 2006, 26: 2373-2380.
[46] TANG Z H, WILLIAMS J J, THOM A J, AKINC M. High temperature oxidation behavior of Ti5Si3-based intermetallics [J]. Intermetallics, 2008, 16: 1118-1124.
[47] SCHNEIBEL J H, RAWN C J, PAYZANT E A, FU C L. Controlling the thermal expansion anisotropy of Mo5Si3 and Ti5Si3 silicides [J]. Intermetallics, 2004, 12: 845-850.
[48] IKARASHI Y, ISHIZAKI K, NAGAI T, HASHIZUKA Y, KONDO Y. Reduction of thermal expansion anisotropy for intermetallie suicides of 16H crystal structure [J]. Intermetallics 1996, 4:S141.
[49] WARD-CLOSE C M, MINOR R, DOORBAR P J. Intermetallic-matrix composites - a review [J]. Intermetallics [J]. 1996, 4: 217-229.
[50] SHON I J, MUNIR Z A. Electric field-activated combustion synthesis of Ti5Si3-Nb and Ti5Si3-ZrO2 composites [J]. J. Mater. Sci., 1997, 32: 5805-5810.
[51] SHON I J, KIM H C, RHO D H, MUNIR Z A. Simultaneous synthesis and densification of Ti5Si3 and Ti5Si3-20 vol% ZrO2 composites by field-activated and pressure-assisted combustion [J]. Mater. Sci. Eng., 1999, A269: 129-135.
[52]李建林,江东亮,谭寿洪.原位生成TiC/Ti5Si3纳米复合材料的显微结构研究[J].无机材料学报, 2000, 15: 336-340.
[53]李建林,江东亮,谭寿洪.原位生成TiC/Ti5Si3纳米复合材料的显微结构[J].金属学报, 1999, 35: 893-896.
[54] WANG L, JIANG W, QIN C, CHEN L. Effect of starting SiC particle size on in situ fabrication of Ti5Si3/TiC composites [J]. Mater. Sci. Eng., 2006, A425: 219-224.
[55] LIN ZJ, ZHOU M J, ZHOU Y C, LI M S, WANG J Y. Microstructural relationships between compounds in the Ti-Si-C system [J]. Scripta Mater., 2006, 55: 445-448.
[56] YEH C L, TENG G S. Use of si3n4 as a reactant in preparation of tin-ti5si3 composites by solid-state shs reactions [J]. J. Alloys. Comp., 2007, 429: 126-132.
[57] ALMAN DE. Reactive sintering of TiAl-Ti5Si3 in situ composites [J]. Intermetallics, 2005, 13: 572-579.
[58] KLASSEN T, SURYANARAYANA C, BORMANN R. Low-temperature superplasticity in ultrafine-grained Ti5Si3-TiAl composites [J]. Script Mater., 2008, 59: 455-458.
[59] RAO K P, ZHOU J B. Charecterization of mechanically alloyed Ti-Al-Si powder blends and their subsequent thermal stability [J]. Mater. Sci. Eng., 2002, A338: 282-294.
[60] RAO K P, ZHOU J B. Charecterization and mechanical properties of in situ synthesized Ti5Si3 /TiAl composites [J]. Mater. Sci. Eng., 2003, A356: 208-218.
[61] GUAN Z Q, PFULLMANN T, OEHRING M, BORMANN R. Phase formation during ball milling and subsequent thermal decomposition of Ti-Al-Si powder blends [J]. J. Alloy. Compd., 1997, 252: 245-251.
[62] YEH C L, LI R F. Formation of TiAl-Ti5Si3 and TiAl -Al2O3 in situ composites by combustion synthesis [J]. Intermetallics, 2008, 16: 64-70.
[63] VOJTECH D, NOVAK M, NOVAK P, LEJCEK P, KOPECEK J. Unidirectional crystallization and high-temperature oxidation of in situ Ti3(Al,Si)-Ti5(Si,Al)3 composite [J]. Mater. Sci. Eng., 2008, A489: 1-10.
[64]李世龙. Ni掺杂下Ti5Si3的燃烧合成反应路径及电子结构计算[D].长春:吉林大学材料学院,2009.
[65] LIANG Y J, CHEN Y C. Data handbook of Mineral Thermodynamics [M]. edited by Northeastern Press, 1993 (in China).
[66] BRAIN I. Thermochemical Data of Pure Substance [M]. 3rd ed., WILEY-VCH Verlag GmbH: 1995.
[67] HOLT J, MUNIR Z A. Combustion synthesis of titanium carbide: theory and experiment [J]. J. Mater. Sci., 1986, 21: 251.
[68] SENKOV O N, Cavusoglu M, Froes F H. Synthesis and characterization of a TiAl/Ti5Si3 composite with a submicrocrystalline structure [J]. Mater. Sci. Eng. 2001, A300: 85-93.
[69] DU Y J, RAO K P, CHUNG J C Y, HAN X D. Phase transitions in reactive formation of Ti5Si3/TiAl in situ composites [J]. Metall. Mater. Trans. 2000, A31: 763-771.
[70] CUPTA S P. Intermetallic compounds in diffusion couples of Ti with an Al-Si eutectic alloy [J].Mater. Charact. 2003, 493: 21-330.
[71] CHRYSANTHOU A, OPOKU E K. HAN L. An investigation of the self-propagating high-temperature synthesis of Ti(Si,Al)2 [J]. J. Mater. Sci. 2005, 40: 2579-2581.
[72] MASSALSKI T B. ET AL. Binary Alloy Phase Diagrams [J]. 2nd ed., USA: ASM international Materials Park, OH, 1990.
[73] FU M. A study of micropyretic reactions in the Mo-Si-Al ternary system [J]. J. Mater.Res.1997, 12: 1481-1491.
[74] WANG T, ZHANG J. Thermoanalytical and metallographical investigations on the synthesis of TiAl3 from elementary powders [J]. Mater. Chem.Phys.2006, 99: 20-25.
[75] NASSAJ E T, KOBASHI M. CHOH T. Fabrication and analysis of in situ formed boride/Al composites by reactive spontaneous infiltration [J]. Script Mater. 1997, 37: 605-614.
[76] BRINKMAN H J, DUSZCZYK J, KATGERMAN L. In-situ formation of TiB2 in a P/M aluminum matrix [J]. Scr. Mater. 1997, 37: 293-3297.
[77] WANG H Y, JIANG Q C, LI X L, WANG J G.In situ synthesis of TiC/Mg composites in molten magnesium [J]. Script Mater. 2003,48: 1349–1354.
[78] LEE S H, LEE J H, LEE Y H, SHIN D H, KIM Y S. Effect of heating rate on the combustion synthesis of intermetallics [J]. Mater. Sci. Eng. 2000, A281: 275–285.
[79] BISWAS A, ROY S K, GURUMURTHY K R, PRABHU N, BANERJEE S. A study of self-propagating high-temperature synthesis of NiAl in thermal explosion mode [J]. Acta Mater. 2002, 50:757-773.
[80] YI H C, PETRIC A, MOORE J J. Effect of heating rate on the combustion synthesis of Ti-Al intermetallic compounds [J]. J. Mater. Sci. 1992, 27: 6797-6806.
[81] Powder Diffraction File Card No. 29–1362 for Ti5Si3 and 37-1449 for TiAl3 (CD ROM), International Center for Diffraction Data (ICDD) [M]. Newtown Square, PA.
[82] VEHOFF H, REUSS S, VOGT W, SPECHT P, Structure Intermetallics 1993, 657-663.
[83] WU J S, BEAVEN P A, WAGNER R. The Ti3(AI,Si)+Ti5(Si,AI)3 eutectic reaction in the Ti-A1-Si system [J]. Scr. Metall, 1990,24:207-212.
[84] J. WU, G. QIU AND L. ZHANG, Theβ-Ti(Al,Si)+Ti5(Si,Al)3 eutectic reaction in the Ti-Al-Si ternary system [J]. Scr Met Mater. 1994, 30: 213-218.
[85] BRUKL C, NOWOTNY H, SCHOB O, BENESOVSKY F. The crystal structure of TiSi, Ti(Al,Si)2 and Mo(Al,Si)2. [J]. Chem. Monthly, German: 1961, 92: 781-788.
[86] RAMAN A, SCHUBERT K. On the constitution of some alloy series related to TiAl3: II. Investigation on some systems Ti-Al-Si and T4..6 [J]. Z Metkd: 1965; 56: 44-52.
[87] YI H C, MOORE J J. Review of self-propagating high temperature (combustion) synthesis (SHS) of powder-compacted materials [J]. J. Mater.sci. 1990, 25: 1159-1168.
[88] MILMAN Y V, MIRACLE B, CHUGUNOVA S I, VOSKOBOINIK I V, KORZHOVA N P, LEGKAYA T N, PODREZOV Y N. Mechanical behavior of Al3Ti intermetallic and L12 phases on its basis [J]. Intermetallics, 2001, 9: 839.
[89] THOM A J, MEYER M K, KIM Y, AKINC M, RAVI V A, SRIVATSAN T S, MOORE J J, Processing
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