Experimental investigations and thermodynamic calculations of the structural and phase composition in the Ti–Si–C system
Abstract Thermodynamic calculations of the structural-phase equilibrium in the Ti–Si–C system at 1100–1400°C are performed using the CALPHAD method. Calculated phase diagrams of this system are presented. It is established that 100% of the $ Ti_{3} %$ SiC_{2} $ phase is formed with the stoichiometri...
Ausführliche Beschreibung
Gespeichert in:
| Autor*in: |
Popov, V. V. [verfasserIn] Gorbachev, I. I. [verfasserIn] Pasynkov, A. Yu. [verfasserIn] Kachenyuk, M. N. [verfasserIn] Somov, O. V. [verfasserIn] |
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| Format: |
E-Artikel |
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| Sprache: |
Englisch |
| Erschienen: |
2017 |
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| Schlagwörter: |
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| Übergeordnetes Werk: |
Enthalten in: Russian journal of non-ferrous metals - New York, NY : Allerton Press, 2007, 58(2017), 5 vom: Sept., Seite 552-559 |
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| Übergeordnetes Werk: |
volume:58 ; year:2017 ; number:5 ; month:09 ; pages:552-559 |
| Links: |
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| DOI / URN: |
10.3103/S1067821217050145 |
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| Katalog-ID: |
SPR023435305 |
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| 245 | 1 | 0 | |a Experimental investigations and thermodynamic calculations of the structural and phase composition in the Ti–Si–C system |
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| 520 | |a Abstract Thermodynamic calculations of the structural-phase equilibrium in the Ti–Si–C system at 1100–1400°C are performed using the CALPHAD method. Calculated phase diagrams of this system are presented. It is established that 100% of the $ Ti_{3} %$ SiC_{2} $ phase is formed with the stoichiometric component ratio. With the deviation of the carbon or silicon content, titanium carbide, titanium disilicide, or silicon carbide appear in the system. The temperature almost does not affect the phase composition in the studied temperature range. The calculated data are compared with the experimental determination of the phase composition of the samples of the mentioned system after the spark-plasma sintering of the mechanically activated powder composition. In practice, the process temperature and duration of high-temperature holding substantially affect the phase composition of the final product, which is associated with the limited rate of solid-phase reactions during the synthesis of compounds. The samples have a grain size of 1–5 μm and hardness of 4–15 GPa, depending the phase composition. | ||
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| 650 | 4 | |a phase diagrams |7 (dpeaa)DE-He213 | |
| 650 | 4 | |a titanium silicon carbide |7 (dpeaa)DE-He213 | |
| 650 | 4 | |a spark-plasma sintering |7 (dpeaa)DE-He213 | |
| 650 | 4 | |a phase formation |7 (dpeaa)DE-He213 | |
| 700 | 1 | |a Gorbachev, I. I. |e verfasserin |4 aut | |
| 700 | 1 | |a Pasynkov, A. Yu. |e verfasserin |4 aut | |
| 700 | 1 | |a Kachenyuk, M. N. |e verfasserin |4 aut | |
| 700 | 1 | |a Somov, O. V. |e verfasserin |4 aut | |
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10.3103/S1067821217050145 doi (DE-627)SPR023435305 (SPR)S1067821217050145-e DE-627 ger DE-627 rakwb eng 620 660 ASE Popov, V. V. verfasserin aut Experimental investigations and thermodynamic calculations of the structural and phase composition in the Ti–Si–C system 2017 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier Abstract Thermodynamic calculations of the structural-phase equilibrium in the Ti–Si–C system at 1100–1400°C are performed using the CALPHAD method. Calculated phase diagrams of this system are presented. It is established that 100% of the $ Ti_{3} %$ SiC_{2} $ phase is formed with the stoichiometric component ratio. With the deviation of the carbon or silicon content, titanium carbide, titanium disilicide, or silicon carbide appear in the system. The temperature almost does not affect the phase composition in the studied temperature range. The calculated data are compared with the experimental determination of the phase composition of the samples of the mentioned system after the spark-plasma sintering of the mechanically activated powder composition. In practice, the process temperature and duration of high-temperature holding substantially affect the phase composition of the final product, which is associated with the limited rate of solid-phase reactions during the synthesis of compounds. The samples have a grain size of 1–5 μm and hardness of 4–15 GPa, depending the phase composition. thermodynamic calculations (dpeaa)DE-He213 phase diagrams (dpeaa)DE-He213 titanium silicon carbide (dpeaa)DE-He213 spark-plasma sintering (dpeaa)DE-He213 phase formation (dpeaa)DE-He213 Gorbachev, I. I. verfasserin aut Pasynkov, A. Yu. verfasserin aut Kachenyuk, M. N. verfasserin aut Somov, O. V. verfasserin aut Enthalten in Russian journal of non-ferrous metals New York, NY : Allerton Press, 2007 58(2017), 5 vom: Sept., Seite 552-559 (DE-627)531202909 (DE-600)2323641-3 1934-970X nnns volume:58 year:2017 number:5 month:09 pages:552-559 https://dx.doi.org/10.3103/S1067821217050145 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_11 GBV_ILN_20 GBV_ILN_22 GBV_ILN_23 GBV_ILN_24 GBV_ILN_31 GBV_ILN_32 GBV_ILN_39 GBV_ILN_40 GBV_ILN_60 GBV_ILN_62 GBV_ILN_63 GBV_ILN_65 GBV_ILN_69 GBV_ILN_70 GBV_ILN_73 GBV_ILN_74 GBV_ILN_90 GBV_ILN_95 GBV_ILN_100 GBV_ILN_105 GBV_ILN_110 GBV_ILN_120 GBV_ILN_138 GBV_ILN_150 GBV_ILN_151 GBV_ILN_152 GBV_ILN_161 GBV_ILN_170 GBV_ILN_171 GBV_ILN_187 GBV_ILN_213 GBV_ILN_224 GBV_ILN_230 GBV_ILN_250 GBV_ILN_281 GBV_ILN_285 GBV_ILN_293 GBV_ILN_370 GBV_ILN_602 GBV_ILN_636 GBV_ILN_702 GBV_ILN_2001 GBV_ILN_2003 GBV_ILN_2004 GBV_ILN_2005 GBV_ILN_2006 GBV_ILN_2007 GBV_ILN_2008 GBV_ILN_2009 GBV_ILN_2010 GBV_ILN_2011 GBV_ILN_2014 GBV_ILN_2015 GBV_ILN_2020 GBV_ILN_2021 GBV_ILN_2025 GBV_ILN_2026 GBV_ILN_2027 GBV_ILN_2031 GBV_ILN_2034 GBV_ILN_2037 GBV_ILN_2038 GBV_ILN_2039 GBV_ILN_2044 GBV_ILN_2048 GBV_ILN_2049 GBV_ILN_2050 GBV_ILN_2055 GBV_ILN_2057 GBV_ILN_2059 GBV_ILN_2061 GBV_ILN_2064 GBV_ILN_2065 GBV_ILN_2068 GBV_ILN_2070 GBV_ILN_2086 GBV_ILN_2088 GBV_ILN_2093 GBV_ILN_2106 GBV_ILN_2107 GBV_ILN_2108 GBV_ILN_2110 GBV_ILN_2111 GBV_ILN_2112 GBV_ILN_2113 GBV_ILN_2116 GBV_ILN_2118 GBV_ILN_2119 GBV_ILN_2122 GBV_ILN_2129 GBV_ILN_2143 GBV_ILN_2144 GBV_ILN_2147 GBV_ILN_2148 GBV_ILN_2152 GBV_ILN_2153 GBV_ILN_2188 GBV_ILN_2190 GBV_ILN_2232 GBV_ILN_2336 GBV_ILN_2446 GBV_ILN_2470 GBV_ILN_2472 GBV_ILN_2507 GBV_ILN_2522 GBV_ILN_2548 GBV_ILN_4035 GBV_ILN_4037 GBV_ILN_4046 GBV_ILN_4112 GBV_ILN_4125 GBV_ILN_4242 GBV_ILN_4246 GBV_ILN_4249 GBV_ILN_4251 GBV_ILN_4305 GBV_ILN_4306 GBV_ILN_4307 GBV_ILN_4313 GBV_ILN_4322 GBV_ILN_4323 GBV_ILN_4324 GBV_ILN_4325 GBV_ILN_4326 GBV_ILN_4333 GBV_ILN_4334 GBV_ILN_4335 GBV_ILN_4336 GBV_ILN_4338 GBV_ILN_4393 GBV_ILN_4700 AR 58 2017 5 09 552-559 |
| spelling |
10.3103/S1067821217050145 doi (DE-627)SPR023435305 (SPR)S1067821217050145-e DE-627 ger DE-627 rakwb eng 620 660 ASE Popov, V. V. verfasserin aut Experimental investigations and thermodynamic calculations of the structural and phase composition in the Ti–Si–C system 2017 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier Abstract Thermodynamic calculations of the structural-phase equilibrium in the Ti–Si–C system at 1100–1400°C are performed using the CALPHAD method. Calculated phase diagrams of this system are presented. It is established that 100% of the $ Ti_{3} %$ SiC_{2} $ phase is formed with the stoichiometric component ratio. With the deviation of the carbon or silicon content, titanium carbide, titanium disilicide, or silicon carbide appear in the system. The temperature almost does not affect the phase composition in the studied temperature range. The calculated data are compared with the experimental determination of the phase composition of the samples of the mentioned system after the spark-plasma sintering of the mechanically activated powder composition. In practice, the process temperature and duration of high-temperature holding substantially affect the phase composition of the final product, which is associated with the limited rate of solid-phase reactions during the synthesis of compounds. The samples have a grain size of 1–5 μm and hardness of 4–15 GPa, depending the phase composition. thermodynamic calculations (dpeaa)DE-He213 phase diagrams (dpeaa)DE-He213 titanium silicon carbide (dpeaa)DE-He213 spark-plasma sintering (dpeaa)DE-He213 phase formation (dpeaa)DE-He213 Gorbachev, I. I. verfasserin aut Pasynkov, A. Yu. verfasserin aut Kachenyuk, M. N. verfasserin aut Somov, O. V. verfasserin aut Enthalten in Russian journal of non-ferrous metals New York, NY : Allerton Press, 2007 58(2017), 5 vom: Sept., Seite 552-559 (DE-627)531202909 (DE-600)2323641-3 1934-970X nnns volume:58 year:2017 number:5 month:09 pages:552-559 https://dx.doi.org/10.3103/S1067821217050145 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_11 GBV_ILN_20 GBV_ILN_22 GBV_ILN_23 GBV_ILN_24 GBV_ILN_31 GBV_ILN_32 GBV_ILN_39 GBV_ILN_40 GBV_ILN_60 GBV_ILN_62 GBV_ILN_63 GBV_ILN_65 GBV_ILN_69 GBV_ILN_70 GBV_ILN_73 GBV_ILN_74 GBV_ILN_90 GBV_ILN_95 GBV_ILN_100 GBV_ILN_105 GBV_ILN_110 GBV_ILN_120 GBV_ILN_138 GBV_ILN_150 GBV_ILN_151 GBV_ILN_152 GBV_ILN_161 GBV_ILN_170 GBV_ILN_171 GBV_ILN_187 GBV_ILN_213 GBV_ILN_224 GBV_ILN_230 GBV_ILN_250 GBV_ILN_281 GBV_ILN_285 GBV_ILN_293 GBV_ILN_370 GBV_ILN_602 GBV_ILN_636 GBV_ILN_702 GBV_ILN_2001 GBV_ILN_2003 GBV_ILN_2004 GBV_ILN_2005 GBV_ILN_2006 GBV_ILN_2007 GBV_ILN_2008 GBV_ILN_2009 GBV_ILN_2010 GBV_ILN_2011 GBV_ILN_2014 GBV_ILN_2015 GBV_ILN_2020 GBV_ILN_2021 GBV_ILN_2025 GBV_ILN_2026 GBV_ILN_2027 GBV_ILN_2031 GBV_ILN_2034 GBV_ILN_2037 GBV_ILN_2038 GBV_ILN_2039 GBV_ILN_2044 GBV_ILN_2048 GBV_ILN_2049 GBV_ILN_2050 GBV_ILN_2055 GBV_ILN_2057 GBV_ILN_2059 GBV_ILN_2061 GBV_ILN_2064 GBV_ILN_2065 GBV_ILN_2068 GBV_ILN_2070 GBV_ILN_2086 GBV_ILN_2088 GBV_ILN_2093 GBV_ILN_2106 GBV_ILN_2107 GBV_ILN_2108 GBV_ILN_2110 GBV_ILN_2111 GBV_ILN_2112 GBV_ILN_2113 GBV_ILN_2116 GBV_ILN_2118 GBV_ILN_2119 GBV_ILN_2122 GBV_ILN_2129 GBV_ILN_2143 GBV_ILN_2144 GBV_ILN_2147 GBV_ILN_2148 GBV_ILN_2152 GBV_ILN_2153 GBV_ILN_2188 GBV_ILN_2190 GBV_ILN_2232 GBV_ILN_2336 GBV_ILN_2446 GBV_ILN_2470 GBV_ILN_2472 GBV_ILN_2507 GBV_ILN_2522 GBV_ILN_2548 GBV_ILN_4035 GBV_ILN_4037 GBV_ILN_4046 GBV_ILN_4112 GBV_ILN_4125 GBV_ILN_4242 GBV_ILN_4246 GBV_ILN_4249 GBV_ILN_4251 GBV_ILN_4305 GBV_ILN_4306 GBV_ILN_4307 GBV_ILN_4313 GBV_ILN_4322 GBV_ILN_4323 GBV_ILN_4324 GBV_ILN_4325 GBV_ILN_4326 GBV_ILN_4333 GBV_ILN_4334 GBV_ILN_4335 GBV_ILN_4336 GBV_ILN_4338 GBV_ILN_4393 GBV_ILN_4700 AR 58 2017 5 09 552-559 |
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10.3103/S1067821217050145 doi (DE-627)SPR023435305 (SPR)S1067821217050145-e DE-627 ger DE-627 rakwb eng 620 660 ASE Popov, V. V. verfasserin aut Experimental investigations and thermodynamic calculations of the structural and phase composition in the Ti–Si–C system 2017 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier Abstract Thermodynamic calculations of the structural-phase equilibrium in the Ti–Si–C system at 1100–1400°C are performed using the CALPHAD method. Calculated phase diagrams of this system are presented. It is established that 100% of the $ Ti_{3} %$ SiC_{2} $ phase is formed with the stoichiometric component ratio. With the deviation of the carbon or silicon content, titanium carbide, titanium disilicide, or silicon carbide appear in the system. The temperature almost does not affect the phase composition in the studied temperature range. The calculated data are compared with the experimental determination of the phase composition of the samples of the mentioned system after the spark-plasma sintering of the mechanically activated powder composition. In practice, the process temperature and duration of high-temperature holding substantially affect the phase composition of the final product, which is associated with the limited rate of solid-phase reactions during the synthesis of compounds. The samples have a grain size of 1–5 μm and hardness of 4–15 GPa, depending the phase composition. thermodynamic calculations (dpeaa)DE-He213 phase diagrams (dpeaa)DE-He213 titanium silicon carbide (dpeaa)DE-He213 spark-plasma sintering (dpeaa)DE-He213 phase formation (dpeaa)DE-He213 Gorbachev, I. I. verfasserin aut Pasynkov, A. Yu. verfasserin aut Kachenyuk, M. N. verfasserin aut Somov, O. V. verfasserin aut Enthalten in Russian journal of non-ferrous metals New York, NY : Allerton Press, 2007 58(2017), 5 vom: Sept., Seite 552-559 (DE-627)531202909 (DE-600)2323641-3 1934-970X nnns volume:58 year:2017 number:5 month:09 pages:552-559 https://dx.doi.org/10.3103/S1067821217050145 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_11 GBV_ILN_20 GBV_ILN_22 GBV_ILN_23 GBV_ILN_24 GBV_ILN_31 GBV_ILN_32 GBV_ILN_39 GBV_ILN_40 GBV_ILN_60 GBV_ILN_62 GBV_ILN_63 GBV_ILN_65 GBV_ILN_69 GBV_ILN_70 GBV_ILN_73 GBV_ILN_74 GBV_ILN_90 GBV_ILN_95 GBV_ILN_100 GBV_ILN_105 GBV_ILN_110 GBV_ILN_120 GBV_ILN_138 GBV_ILN_150 GBV_ILN_151 GBV_ILN_152 GBV_ILN_161 GBV_ILN_170 GBV_ILN_171 GBV_ILN_187 GBV_ILN_213 GBV_ILN_224 GBV_ILN_230 GBV_ILN_250 GBV_ILN_281 GBV_ILN_285 GBV_ILN_293 GBV_ILN_370 GBV_ILN_602 GBV_ILN_636 GBV_ILN_702 GBV_ILN_2001 GBV_ILN_2003 GBV_ILN_2004 GBV_ILN_2005 GBV_ILN_2006 GBV_ILN_2007 GBV_ILN_2008 GBV_ILN_2009 GBV_ILN_2010 GBV_ILN_2011 GBV_ILN_2014 GBV_ILN_2015 GBV_ILN_2020 GBV_ILN_2021 GBV_ILN_2025 GBV_ILN_2026 GBV_ILN_2027 GBV_ILN_2031 GBV_ILN_2034 GBV_ILN_2037 GBV_ILN_2038 GBV_ILN_2039 GBV_ILN_2044 GBV_ILN_2048 GBV_ILN_2049 GBV_ILN_2050 GBV_ILN_2055 GBV_ILN_2057 GBV_ILN_2059 GBV_ILN_2061 GBV_ILN_2064 GBV_ILN_2065 GBV_ILN_2068 GBV_ILN_2070 GBV_ILN_2086 GBV_ILN_2088 GBV_ILN_2093 GBV_ILN_2106 GBV_ILN_2107 GBV_ILN_2108 GBV_ILN_2110 GBV_ILN_2111 GBV_ILN_2112 GBV_ILN_2113 GBV_ILN_2116 GBV_ILN_2118 GBV_ILN_2119 GBV_ILN_2122 GBV_ILN_2129 GBV_ILN_2143 GBV_ILN_2144 GBV_ILN_2147 GBV_ILN_2148 GBV_ILN_2152 GBV_ILN_2153 GBV_ILN_2188 GBV_ILN_2190 GBV_ILN_2232 GBV_ILN_2336 GBV_ILN_2446 GBV_ILN_2470 GBV_ILN_2472 GBV_ILN_2507 GBV_ILN_2522 GBV_ILN_2548 GBV_ILN_4035 GBV_ILN_4037 GBV_ILN_4046 GBV_ILN_4112 GBV_ILN_4125 GBV_ILN_4242 GBV_ILN_4246 GBV_ILN_4249 GBV_ILN_4251 GBV_ILN_4305 GBV_ILN_4306 GBV_ILN_4307 GBV_ILN_4313 GBV_ILN_4322 GBV_ILN_4323 GBV_ILN_4324 GBV_ILN_4325 GBV_ILN_4326 GBV_ILN_4333 GBV_ILN_4334 GBV_ILN_4335 GBV_ILN_4336 GBV_ILN_4338 GBV_ILN_4393 GBV_ILN_4700 AR 58 2017 5 09 552-559 |
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10.3103/S1067821217050145 doi (DE-627)SPR023435305 (SPR)S1067821217050145-e DE-627 ger DE-627 rakwb eng 620 660 ASE Popov, V. V. verfasserin aut Experimental investigations and thermodynamic calculations of the structural and phase composition in the Ti–Si–C system 2017 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier Abstract Thermodynamic calculations of the structural-phase equilibrium in the Ti–Si–C system at 1100–1400°C are performed using the CALPHAD method. Calculated phase diagrams of this system are presented. It is established that 100% of the $ Ti_{3} %$ SiC_{2} $ phase is formed with the stoichiometric component ratio. With the deviation of the carbon or silicon content, titanium carbide, titanium disilicide, or silicon carbide appear in the system. The temperature almost does not affect the phase composition in the studied temperature range. The calculated data are compared with the experimental determination of the phase composition of the samples of the mentioned system after the spark-plasma sintering of the mechanically activated powder composition. In practice, the process temperature and duration of high-temperature holding substantially affect the phase composition of the final product, which is associated with the limited rate of solid-phase reactions during the synthesis of compounds. The samples have a grain size of 1–5 μm and hardness of 4–15 GPa, depending the phase composition. thermodynamic calculations (dpeaa)DE-He213 phase diagrams (dpeaa)DE-He213 titanium silicon carbide (dpeaa)DE-He213 spark-plasma sintering (dpeaa)DE-He213 phase formation (dpeaa)DE-He213 Gorbachev, I. I. verfasserin aut Pasynkov, A. Yu. verfasserin aut Kachenyuk, M. N. verfasserin aut Somov, O. V. verfasserin aut Enthalten in Russian journal of non-ferrous metals New York, NY : Allerton Press, 2007 58(2017), 5 vom: Sept., Seite 552-559 (DE-627)531202909 (DE-600)2323641-3 1934-970X nnns volume:58 year:2017 number:5 month:09 pages:552-559 https://dx.doi.org/10.3103/S1067821217050145 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_11 GBV_ILN_20 GBV_ILN_22 GBV_ILN_23 GBV_ILN_24 GBV_ILN_31 GBV_ILN_32 GBV_ILN_39 GBV_ILN_40 GBV_ILN_60 GBV_ILN_62 GBV_ILN_63 GBV_ILN_65 GBV_ILN_69 GBV_ILN_70 GBV_ILN_73 GBV_ILN_74 GBV_ILN_90 GBV_ILN_95 GBV_ILN_100 GBV_ILN_105 GBV_ILN_110 GBV_ILN_120 GBV_ILN_138 GBV_ILN_150 GBV_ILN_151 GBV_ILN_152 GBV_ILN_161 GBV_ILN_170 GBV_ILN_171 GBV_ILN_187 GBV_ILN_213 GBV_ILN_224 GBV_ILN_230 GBV_ILN_250 GBV_ILN_281 GBV_ILN_285 GBV_ILN_293 GBV_ILN_370 GBV_ILN_602 GBV_ILN_636 GBV_ILN_702 GBV_ILN_2001 GBV_ILN_2003 GBV_ILN_2004 GBV_ILN_2005 GBV_ILN_2006 GBV_ILN_2007 GBV_ILN_2008 GBV_ILN_2009 GBV_ILN_2010 GBV_ILN_2011 GBV_ILN_2014 GBV_ILN_2015 GBV_ILN_2020 GBV_ILN_2021 GBV_ILN_2025 GBV_ILN_2026 GBV_ILN_2027 GBV_ILN_2031 GBV_ILN_2034 GBV_ILN_2037 GBV_ILN_2038 GBV_ILN_2039 GBV_ILN_2044 GBV_ILN_2048 GBV_ILN_2049 GBV_ILN_2050 GBV_ILN_2055 GBV_ILN_2057 GBV_ILN_2059 GBV_ILN_2061 GBV_ILN_2064 GBV_ILN_2065 GBV_ILN_2068 GBV_ILN_2070 GBV_ILN_2086 GBV_ILN_2088 GBV_ILN_2093 GBV_ILN_2106 GBV_ILN_2107 GBV_ILN_2108 GBV_ILN_2110 GBV_ILN_2111 GBV_ILN_2112 GBV_ILN_2113 GBV_ILN_2116 GBV_ILN_2118 GBV_ILN_2119 GBV_ILN_2122 GBV_ILN_2129 GBV_ILN_2143 GBV_ILN_2144 GBV_ILN_2147 GBV_ILN_2148 GBV_ILN_2152 GBV_ILN_2153 GBV_ILN_2188 GBV_ILN_2190 GBV_ILN_2232 GBV_ILN_2336 GBV_ILN_2446 GBV_ILN_2470 GBV_ILN_2472 GBV_ILN_2507 GBV_ILN_2522 GBV_ILN_2548 GBV_ILN_4035 GBV_ILN_4037 GBV_ILN_4046 GBV_ILN_4112 GBV_ILN_4125 GBV_ILN_4242 GBV_ILN_4246 GBV_ILN_4249 GBV_ILN_4251 GBV_ILN_4305 GBV_ILN_4306 GBV_ILN_4307 GBV_ILN_4313 GBV_ILN_4322 GBV_ILN_4323 GBV_ILN_4324 GBV_ILN_4325 GBV_ILN_4326 GBV_ILN_4333 GBV_ILN_4334 GBV_ILN_4335 GBV_ILN_4336 GBV_ILN_4338 GBV_ILN_4393 GBV_ILN_4700 AR 58 2017 5 09 552-559 |
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10.3103/S1067821217050145 doi (DE-627)SPR023435305 (SPR)S1067821217050145-e DE-627 ger DE-627 rakwb eng 620 660 ASE Popov, V. V. verfasserin aut Experimental investigations and thermodynamic calculations of the structural and phase composition in the Ti–Si–C system 2017 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier Abstract Thermodynamic calculations of the structural-phase equilibrium in the Ti–Si–C system at 1100–1400°C are performed using the CALPHAD method. Calculated phase diagrams of this system are presented. It is established that 100% of the $ Ti_{3} %$ SiC_{2} $ phase is formed with the stoichiometric component ratio. With the deviation of the carbon or silicon content, titanium carbide, titanium disilicide, or silicon carbide appear in the system. The temperature almost does not affect the phase composition in the studied temperature range. The calculated data are compared with the experimental determination of the phase composition of the samples of the mentioned system after the spark-plasma sintering of the mechanically activated powder composition. In practice, the process temperature and duration of high-temperature holding substantially affect the phase composition of the final product, which is associated with the limited rate of solid-phase reactions during the synthesis of compounds. The samples have a grain size of 1–5 μm and hardness of 4–15 GPa, depending the phase composition. thermodynamic calculations (dpeaa)DE-He213 phase diagrams (dpeaa)DE-He213 titanium silicon carbide (dpeaa)DE-He213 spark-plasma sintering (dpeaa)DE-He213 phase formation (dpeaa)DE-He213 Gorbachev, I. I. verfasserin aut Pasynkov, A. Yu. verfasserin aut Kachenyuk, M. N. verfasserin aut Somov, O. V. verfasserin aut Enthalten in Russian journal of non-ferrous metals New York, NY : Allerton Press, 2007 58(2017), 5 vom: Sept., Seite 552-559 (DE-627)531202909 (DE-600)2323641-3 1934-970X nnns volume:58 year:2017 number:5 month:09 pages:552-559 https://dx.doi.org/10.3103/S1067821217050145 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_11 GBV_ILN_20 GBV_ILN_22 GBV_ILN_23 GBV_ILN_24 GBV_ILN_31 GBV_ILN_32 GBV_ILN_39 GBV_ILN_40 GBV_ILN_60 GBV_ILN_62 GBV_ILN_63 GBV_ILN_65 GBV_ILN_69 GBV_ILN_70 GBV_ILN_73 GBV_ILN_74 GBV_ILN_90 GBV_ILN_95 GBV_ILN_100 GBV_ILN_105 GBV_ILN_110 GBV_ILN_120 GBV_ILN_138 GBV_ILN_150 GBV_ILN_151 GBV_ILN_152 GBV_ILN_161 GBV_ILN_170 GBV_ILN_171 GBV_ILN_187 GBV_ILN_213 GBV_ILN_224 GBV_ILN_230 GBV_ILN_250 GBV_ILN_281 GBV_ILN_285 GBV_ILN_293 GBV_ILN_370 GBV_ILN_602 GBV_ILN_636 GBV_ILN_702 GBV_ILN_2001 GBV_ILN_2003 GBV_ILN_2004 GBV_ILN_2005 GBV_ILN_2006 GBV_ILN_2007 GBV_ILN_2008 GBV_ILN_2009 GBV_ILN_2010 GBV_ILN_2011 GBV_ILN_2014 GBV_ILN_2015 GBV_ILN_2020 GBV_ILN_2021 GBV_ILN_2025 GBV_ILN_2026 GBV_ILN_2027 GBV_ILN_2031 GBV_ILN_2034 GBV_ILN_2037 GBV_ILN_2038 GBV_ILN_2039 GBV_ILN_2044 GBV_ILN_2048 GBV_ILN_2049 GBV_ILN_2050 GBV_ILN_2055 GBV_ILN_2057 GBV_ILN_2059 GBV_ILN_2061 GBV_ILN_2064 GBV_ILN_2065 GBV_ILN_2068 GBV_ILN_2070 GBV_ILN_2086 GBV_ILN_2088 GBV_ILN_2093 GBV_ILN_2106 GBV_ILN_2107 GBV_ILN_2108 GBV_ILN_2110 GBV_ILN_2111 GBV_ILN_2112 GBV_ILN_2113 GBV_ILN_2116 GBV_ILN_2118 GBV_ILN_2119 GBV_ILN_2122 GBV_ILN_2129 GBV_ILN_2143 GBV_ILN_2144 GBV_ILN_2147 GBV_ILN_2148 GBV_ILN_2152 GBV_ILN_2153 GBV_ILN_2188 GBV_ILN_2190 GBV_ILN_2232 GBV_ILN_2336 GBV_ILN_2446 GBV_ILN_2470 GBV_ILN_2472 GBV_ILN_2507 GBV_ILN_2522 GBV_ILN_2548 GBV_ILN_4035 GBV_ILN_4037 GBV_ILN_4046 GBV_ILN_4112 GBV_ILN_4125 GBV_ILN_4242 GBV_ILN_4246 GBV_ILN_4249 GBV_ILN_4251 GBV_ILN_4305 GBV_ILN_4306 GBV_ILN_4307 GBV_ILN_4313 GBV_ILN_4322 GBV_ILN_4323 GBV_ILN_4324 GBV_ILN_4325 GBV_ILN_4326 GBV_ILN_4333 GBV_ILN_4334 GBV_ILN_4335 GBV_ILN_4336 GBV_ILN_4338 GBV_ILN_4393 GBV_ILN_4700 AR 58 2017 5 09 552-559 |
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Popov, V. V. @@aut@@ Gorbachev, I. I. @@aut@@ Pasynkov, A. Yu. @@aut@@ Kachenyuk, M. N. @@aut@@ Somov, O. V. @@aut@@ |
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Popov, V. V. |
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Popov, V. V. ddc 620 misc thermodynamic calculations misc phase diagrams misc titanium silicon carbide misc spark-plasma sintering misc phase formation Experimental investigations and thermodynamic calculations of the structural and phase composition in the Ti–Si–C system |
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620 660 ASE Experimental investigations and thermodynamic calculations of the structural and phase composition in the Ti–Si–C system thermodynamic calculations (dpeaa)DE-He213 phase diagrams (dpeaa)DE-He213 titanium silicon carbide (dpeaa)DE-He213 spark-plasma sintering (dpeaa)DE-He213 phase formation (dpeaa)DE-He213 |
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ddc 620 misc thermodynamic calculations misc phase diagrams misc titanium silicon carbide misc spark-plasma sintering misc phase formation |
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Experimental investigations and thermodynamic calculations of the structural and phase composition in the Ti–Si–C system |
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Experimental investigations and thermodynamic calculations of the structural and phase composition in the Ti–Si–C system |
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Russian journal of non-ferrous metals |
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Popov, V. V. Gorbachev, I. I. Pasynkov, A. Yu. Kachenyuk, M. N. Somov, O. V. |
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experimental investigations and thermodynamic calculations of the structural and phase composition in the ti–si–c system |
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Experimental investigations and thermodynamic calculations of the structural and phase composition in the Ti–Si–C system |
| abstract |
Abstract Thermodynamic calculations of the structural-phase equilibrium in the Ti–Si–C system at 1100–1400°C are performed using the CALPHAD method. Calculated phase diagrams of this system are presented. It is established that 100% of the $ Ti_{3} %$ SiC_{2} $ phase is formed with the stoichiometric component ratio. With the deviation of the carbon or silicon content, titanium carbide, titanium disilicide, or silicon carbide appear in the system. The temperature almost does not affect the phase composition in the studied temperature range. The calculated data are compared with the experimental determination of the phase composition of the samples of the mentioned system after the spark-plasma sintering of the mechanically activated powder composition. In practice, the process temperature and duration of high-temperature holding substantially affect the phase composition of the final product, which is associated with the limited rate of solid-phase reactions during the synthesis of compounds. The samples have a grain size of 1–5 μm and hardness of 4–15 GPa, depending the phase composition. |
| abstractGer |
Abstract Thermodynamic calculations of the structural-phase equilibrium in the Ti–Si–C system at 1100–1400°C are performed using the CALPHAD method. Calculated phase diagrams of this system are presented. It is established that 100% of the $ Ti_{3} %$ SiC_{2} $ phase is formed with the stoichiometric component ratio. With the deviation of the carbon or silicon content, titanium carbide, titanium disilicide, or silicon carbide appear in the system. The temperature almost does not affect the phase composition in the studied temperature range. The calculated data are compared with the experimental determination of the phase composition of the samples of the mentioned system after the spark-plasma sintering of the mechanically activated powder composition. In practice, the process temperature and duration of high-temperature holding substantially affect the phase composition of the final product, which is associated with the limited rate of solid-phase reactions during the synthesis of compounds. The samples have a grain size of 1–5 μm and hardness of 4–15 GPa, depending the phase composition. |
| abstract_unstemmed |
Abstract Thermodynamic calculations of the structural-phase equilibrium in the Ti–Si–C system at 1100–1400°C are performed using the CALPHAD method. Calculated phase diagrams of this system are presented. It is established that 100% of the $ Ti_{3} %$ SiC_{2} $ phase is formed with the stoichiometric component ratio. With the deviation of the carbon or silicon content, titanium carbide, titanium disilicide, or silicon carbide appear in the system. The temperature almost does not affect the phase composition in the studied temperature range. The calculated data are compared with the experimental determination of the phase composition of the samples of the mentioned system after the spark-plasma sintering of the mechanically activated powder composition. In practice, the process temperature and duration of high-temperature holding substantially affect the phase composition of the final product, which is associated with the limited rate of solid-phase reactions during the synthesis of compounds. The samples have a grain size of 1–5 μm and hardness of 4–15 GPa, depending the phase composition. |
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Experimental investigations and thermodynamic calculations of the structural and phase composition in the Ti–Si–C system |
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https://dx.doi.org/10.3103/S1067821217050145 |
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Gorbachev, I. I. Pasynkov, A. Yu Kachenyuk, M. N. Somov, O. V. |
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Gorbachev, I. I. Pasynkov, A. Yu Kachenyuk, M. N. Somov, O. V. |
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10.3103/S1067821217050145 |
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2024-07-03T18:55:02.576Z |
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| score |
7.397517 |