Multiple strengthening mechanisms in nanoparticle-reinforced copper matrix composites
Abstract The multiple hardening mechanisms of a copper matrix have been presented and discussed. The pre-alloyed ball milled Cu–3 wt.%Al and the atomized Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ powders have been used as starting materials. Dispersoid particles $ Al_{2} %$ O_{3} $ and TiB$_{{\bf 2}\thinspa...
Ausführliche Beschreibung
Gespeichert in:
| Autor*in: |
BOZIC, D [verfasserIn] STASIC, J [verfasserIn] DIMCIC, B [verfasserIn] VILOTIJEVIC, M [verfasserIn] RAJKOVIC, V [verfasserIn] |
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| Format: |
E-Artikel |
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| Sprache: |
Englisch |
| Erschienen: |
2011 |
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| Schlagwörter: |
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| Übergeordnetes Werk: |
Enthalten in: Bulletin of materials science - Bangalore, 1979, 34(2011), 2 vom: Apr., Seite 217-226 |
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| Übergeordnetes Werk: |
volume:34 ; year:2011 ; number:2 ; month:04 ; pages:217-226 |
| Links: |
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| DOI / URN: |
10.1007/s12034-011-0102-8 |
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| Katalog-ID: |
SPR023925159 |
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| 520 | |a Abstract The multiple hardening mechanisms of a copper matrix have been presented and discussed. The pre-alloyed ball milled Cu–3 wt.%Al and the atomized Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ powders have been used as starting materials. Dispersoid particles $ Al_{2} %$ O_{3} $ and TiB$_{{\bf 2}\thinspace }$were formed in situ. The powders have been hot consolidated. Optical microscopy, SEM, TEM, and X-ray diffraction analysis were performed for microstructural characterization. Increase in microhardness of Cu–3 wt.%Al compacts is a consequence of the crystallite size refinement and the presence of $ Al_{2} %$ O_{3} $ particles. High hardening of Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ is a consequence of the presence of modular structure, $ Cu_{4} %$ Ti_{(m)} $, and $ TiB_{2} $ particles. | ||
| 650 | 4 | |a Metal–matrix composites (MMCs) |7 (dpeaa)DE-He213 | |
| 650 | 4 | |a nanoparticles |7 (dpeaa)DE-He213 | |
| 650 | 4 | |a hardness testing |7 (dpeaa)DE-He213 | |
| 650 | 4 | |a microstructural characterization. |7 (dpeaa)DE-He213 | |
| 700 | 1 | |a STASIC, J |e verfasserin |4 aut | |
| 700 | 1 | |a DIMCIC, B |e verfasserin |4 aut | |
| 700 | 1 | |a VILOTIJEVIC, M |e verfasserin |4 aut | |
| 700 | 1 | |a RAJKOVIC, V |e verfasserin |4 aut | |
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10.1007/s12034-011-0102-8 doi (DE-627)SPR023925159 (SPR)s12034-011-0102-8-e DE-627 ger DE-627 rakwb eng 600 ASE 51.00 bkl BOZIC, D verfasserin aut Multiple strengthening mechanisms in nanoparticle-reinforced copper matrix composites 2011 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier Abstract The multiple hardening mechanisms of a copper matrix have been presented and discussed. The pre-alloyed ball milled Cu–3 wt.%Al and the atomized Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ powders have been used as starting materials. Dispersoid particles $ Al_{2} %$ O_{3} $ and TiB$_{{\bf 2}\thinspace }$were formed in situ. The powders have been hot consolidated. Optical microscopy, SEM, TEM, and X-ray diffraction analysis were performed for microstructural characterization. Increase in microhardness of Cu–3 wt.%Al compacts is a consequence of the crystallite size refinement and the presence of $ Al_{2} %$ O_{3} $ particles. High hardening of Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ is a consequence of the presence of modular structure, $ Cu_{4} %$ Ti_{(m)} $, and $ TiB_{2} $ particles. Metal–matrix composites (MMCs) (dpeaa)DE-He213 nanoparticles (dpeaa)DE-He213 hardness testing (dpeaa)DE-He213 microstructural characterization. (dpeaa)DE-He213 STASIC, J verfasserin aut DIMCIC, B verfasserin aut VILOTIJEVIC, M verfasserin aut RAJKOVIC, V verfasserin aut Enthalten in Bulletin of materials science Bangalore, 1979 34(2011), 2 vom: Apr., Seite 217-226 (DE-627)358454425 (DE-600)2096424-9 0973-7669 nnns volume:34 year:2011 number:2 month:04 pages:217-226 https://dx.doi.org/10.1007/s12034-011-0102-8 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER 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_206 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_2056 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_4012 GBV_ILN_4035 GBV_ILN_4037 GBV_ILN_4046 GBV_ILN_4112 GBV_ILN_4125 GBV_ILN_4126 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_4367 GBV_ILN_4393 GBV_ILN_4700 51.00 ASE AR 34 2011 2 04 217-226 |
| spelling |
10.1007/s12034-011-0102-8 doi (DE-627)SPR023925159 (SPR)s12034-011-0102-8-e DE-627 ger DE-627 rakwb eng 600 ASE 51.00 bkl BOZIC, D verfasserin aut Multiple strengthening mechanisms in nanoparticle-reinforced copper matrix composites 2011 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier Abstract The multiple hardening mechanisms of a copper matrix have been presented and discussed. The pre-alloyed ball milled Cu–3 wt.%Al and the atomized Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ powders have been used as starting materials. Dispersoid particles $ Al_{2} %$ O_{3} $ and TiB$_{{\bf 2}\thinspace }$were formed in situ. The powders have been hot consolidated. Optical microscopy, SEM, TEM, and X-ray diffraction analysis were performed for microstructural characterization. Increase in microhardness of Cu–3 wt.%Al compacts is a consequence of the crystallite size refinement and the presence of $ Al_{2} %$ O_{3} $ particles. High hardening of Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ is a consequence of the presence of modular structure, $ Cu_{4} %$ Ti_{(m)} $, and $ TiB_{2} $ particles. Metal–matrix composites (MMCs) (dpeaa)DE-He213 nanoparticles (dpeaa)DE-He213 hardness testing (dpeaa)DE-He213 microstructural characterization. (dpeaa)DE-He213 STASIC, J verfasserin aut DIMCIC, B verfasserin aut VILOTIJEVIC, M verfasserin aut RAJKOVIC, V verfasserin aut Enthalten in Bulletin of materials science Bangalore, 1979 34(2011), 2 vom: Apr., Seite 217-226 (DE-627)358454425 (DE-600)2096424-9 0973-7669 nnns volume:34 year:2011 number:2 month:04 pages:217-226 https://dx.doi.org/10.1007/s12034-011-0102-8 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER 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_206 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_2056 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_4012 GBV_ILN_4035 GBV_ILN_4037 GBV_ILN_4046 GBV_ILN_4112 GBV_ILN_4125 GBV_ILN_4126 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_4367 GBV_ILN_4393 GBV_ILN_4700 51.00 ASE AR 34 2011 2 04 217-226 |
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10.1007/s12034-011-0102-8 doi (DE-627)SPR023925159 (SPR)s12034-011-0102-8-e DE-627 ger DE-627 rakwb eng 600 ASE 51.00 bkl BOZIC, D verfasserin aut Multiple strengthening mechanisms in nanoparticle-reinforced copper matrix composites 2011 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier Abstract The multiple hardening mechanisms of a copper matrix have been presented and discussed. The pre-alloyed ball milled Cu–3 wt.%Al and the atomized Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ powders have been used as starting materials. Dispersoid particles $ Al_{2} %$ O_{3} $ and TiB$_{{\bf 2}\thinspace }$were formed in situ. The powders have been hot consolidated. Optical microscopy, SEM, TEM, and X-ray diffraction analysis were performed for microstructural characterization. Increase in microhardness of Cu–3 wt.%Al compacts is a consequence of the crystallite size refinement and the presence of $ Al_{2} %$ O_{3} $ particles. High hardening of Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ is a consequence of the presence of modular structure, $ Cu_{4} %$ Ti_{(m)} $, and $ TiB_{2} $ particles. Metal–matrix composites (MMCs) (dpeaa)DE-He213 nanoparticles (dpeaa)DE-He213 hardness testing (dpeaa)DE-He213 microstructural characterization. (dpeaa)DE-He213 STASIC, J verfasserin aut DIMCIC, B verfasserin aut VILOTIJEVIC, M verfasserin aut RAJKOVIC, V verfasserin aut Enthalten in Bulletin of materials science Bangalore, 1979 34(2011), 2 vom: Apr., Seite 217-226 (DE-627)358454425 (DE-600)2096424-9 0973-7669 nnns volume:34 year:2011 number:2 month:04 pages:217-226 https://dx.doi.org/10.1007/s12034-011-0102-8 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER 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_206 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_2056 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_4012 GBV_ILN_4035 GBV_ILN_4037 GBV_ILN_4046 GBV_ILN_4112 GBV_ILN_4125 GBV_ILN_4126 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_4367 GBV_ILN_4393 GBV_ILN_4700 51.00 ASE AR 34 2011 2 04 217-226 |
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10.1007/s12034-011-0102-8 doi (DE-627)SPR023925159 (SPR)s12034-011-0102-8-e DE-627 ger DE-627 rakwb eng 600 ASE 51.00 bkl BOZIC, D verfasserin aut Multiple strengthening mechanisms in nanoparticle-reinforced copper matrix composites 2011 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier Abstract The multiple hardening mechanisms of a copper matrix have been presented and discussed. The pre-alloyed ball milled Cu–3 wt.%Al and the atomized Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ powders have been used as starting materials. Dispersoid particles $ Al_{2} %$ O_{3} $ and TiB$_{{\bf 2}\thinspace }$were formed in situ. The powders have been hot consolidated. Optical microscopy, SEM, TEM, and X-ray diffraction analysis were performed for microstructural characterization. Increase in microhardness of Cu–3 wt.%Al compacts is a consequence of the crystallite size refinement and the presence of $ Al_{2} %$ O_{3} $ particles. High hardening of Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ is a consequence of the presence of modular structure, $ Cu_{4} %$ Ti_{(m)} $, and $ TiB_{2} $ particles. Metal–matrix composites (MMCs) (dpeaa)DE-He213 nanoparticles (dpeaa)DE-He213 hardness testing (dpeaa)DE-He213 microstructural characterization. (dpeaa)DE-He213 STASIC, J verfasserin aut DIMCIC, B verfasserin aut VILOTIJEVIC, M verfasserin aut RAJKOVIC, V verfasserin aut Enthalten in Bulletin of materials science Bangalore, 1979 34(2011), 2 vom: Apr., Seite 217-226 (DE-627)358454425 (DE-600)2096424-9 0973-7669 nnns volume:34 year:2011 number:2 month:04 pages:217-226 https://dx.doi.org/10.1007/s12034-011-0102-8 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER 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_206 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_2056 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_4012 GBV_ILN_4035 GBV_ILN_4037 GBV_ILN_4046 GBV_ILN_4112 GBV_ILN_4125 GBV_ILN_4126 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_4367 GBV_ILN_4393 GBV_ILN_4700 51.00 ASE AR 34 2011 2 04 217-226 |
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10.1007/s12034-011-0102-8 doi (DE-627)SPR023925159 (SPR)s12034-011-0102-8-e DE-627 ger DE-627 rakwb eng 600 ASE 51.00 bkl BOZIC, D verfasserin aut Multiple strengthening mechanisms in nanoparticle-reinforced copper matrix composites 2011 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier Abstract The multiple hardening mechanisms of a copper matrix have been presented and discussed. The pre-alloyed ball milled Cu–3 wt.%Al and the atomized Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ powders have been used as starting materials. Dispersoid particles $ Al_{2} %$ O_{3} $ and TiB$_{{\bf 2}\thinspace }$were formed in situ. The powders have been hot consolidated. Optical microscopy, SEM, TEM, and X-ray diffraction analysis were performed for microstructural characterization. Increase in microhardness of Cu–3 wt.%Al compacts is a consequence of the crystallite size refinement and the presence of $ Al_{2} %$ O_{3} $ particles. High hardening of Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ is a consequence of the presence of modular structure, $ Cu_{4} %$ Ti_{(m)} $, and $ TiB_{2} $ particles. Metal–matrix composites (MMCs) (dpeaa)DE-He213 nanoparticles (dpeaa)DE-He213 hardness testing (dpeaa)DE-He213 microstructural characterization. (dpeaa)DE-He213 STASIC, J verfasserin aut DIMCIC, B verfasserin aut VILOTIJEVIC, M verfasserin aut RAJKOVIC, V verfasserin aut Enthalten in Bulletin of materials science Bangalore, 1979 34(2011), 2 vom: Apr., Seite 217-226 (DE-627)358454425 (DE-600)2096424-9 0973-7669 nnns volume:34 year:2011 number:2 month:04 pages:217-226 https://dx.doi.org/10.1007/s12034-011-0102-8 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER 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_206 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_2056 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_4012 GBV_ILN_4035 GBV_ILN_4037 GBV_ILN_4046 GBV_ILN_4112 GBV_ILN_4125 GBV_ILN_4126 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_4367 GBV_ILN_4393 GBV_ILN_4700 51.00 ASE AR 34 2011 2 04 217-226 |
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BOZIC, D @@aut@@ STASIC, J @@aut@@ DIMCIC, B @@aut@@ VILOTIJEVIC, M @@aut@@ RAJKOVIC, V @@aut@@ |
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| author |
BOZIC, D |
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BOZIC, D ddc 600 bkl 51.00 misc Metal–matrix composites (MMCs) misc nanoparticles misc hardness testing misc microstructural characterization. Multiple strengthening mechanisms in nanoparticle-reinforced copper matrix composites |
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600 ASE 51.00 bkl Multiple strengthening mechanisms in nanoparticle-reinforced copper matrix composites Metal–matrix composites (MMCs) (dpeaa)DE-He213 nanoparticles (dpeaa)DE-He213 hardness testing (dpeaa)DE-He213 microstructural characterization. (dpeaa)DE-He213 |
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ddc 600 bkl 51.00 misc Metal–matrix composites (MMCs) misc nanoparticles misc hardness testing misc microstructural characterization. |
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ddc 600 bkl 51.00 misc Metal–matrix composites (MMCs) misc nanoparticles misc hardness testing misc microstructural characterization. |
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ddc 600 bkl 51.00 misc Metal–matrix composites (MMCs) misc nanoparticles misc hardness testing misc microstructural characterization. |
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Multiple strengthening mechanisms in nanoparticle-reinforced copper matrix composites |
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Multiple strengthening mechanisms in nanoparticle-reinforced copper matrix composites |
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verfasserin |
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multiple strengthening mechanisms in nanoparticle-reinforced copper matrix composites |
| title_auth |
Multiple strengthening mechanisms in nanoparticle-reinforced copper matrix composites |
| abstract |
Abstract The multiple hardening mechanisms of a copper matrix have been presented and discussed. The pre-alloyed ball milled Cu–3 wt.%Al and the atomized Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ powders have been used as starting materials. Dispersoid particles $ Al_{2} %$ O_{3} $ and TiB$_{{\bf 2}\thinspace }$were formed in situ. The powders have been hot consolidated. Optical microscopy, SEM, TEM, and X-ray diffraction analysis were performed for microstructural characterization. Increase in microhardness of Cu–3 wt.%Al compacts is a consequence of the crystallite size refinement and the presence of $ Al_{2} %$ O_{3} $ particles. High hardening of Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ is a consequence of the presence of modular structure, $ Cu_{4} %$ Ti_{(m)} $, and $ TiB_{2} $ particles. |
| abstractGer |
Abstract The multiple hardening mechanisms of a copper matrix have been presented and discussed. The pre-alloyed ball milled Cu–3 wt.%Al and the atomized Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ powders have been used as starting materials. Dispersoid particles $ Al_{2} %$ O_{3} $ and TiB$_{{\bf 2}\thinspace }$were formed in situ. The powders have been hot consolidated. Optical microscopy, SEM, TEM, and X-ray diffraction analysis were performed for microstructural characterization. Increase in microhardness of Cu–3 wt.%Al compacts is a consequence of the crystallite size refinement and the presence of $ Al_{2} %$ O_{3} $ particles. High hardening of Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ is a consequence of the presence of modular structure, $ Cu_{4} %$ Ti_{(m)} $, and $ TiB_{2} $ particles. |
| abstract_unstemmed |
Abstract The multiple hardening mechanisms of a copper matrix have been presented and discussed. The pre-alloyed ball milled Cu–3 wt.%Al and the atomized Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ powders have been used as starting materials. Dispersoid particles $ Al_{2} %$ O_{3} $ and TiB$_{{\bf 2}\thinspace }$were formed in situ. The powders have been hot consolidated. Optical microscopy, SEM, TEM, and X-ray diffraction analysis were performed for microstructural characterization. Increase in microhardness of Cu–3 wt.%Al compacts is a consequence of the crystallite size refinement and the presence of $ Al_{2} %$ O_{3} $ particles. High hardening of Cu–0·6 wt.%Ti–2·5 wt.%$ TiB_{2} $ is a consequence of the presence of modular structure, $ Cu_{4} %$ Ti_{(m)} $, and $ TiB_{2} $ particles. |
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| title_short |
Multiple strengthening mechanisms in nanoparticle-reinforced copper matrix composites |
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https://dx.doi.org/10.1007/s12034-011-0102-8 |
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STASIC, J DIMCIC, B VILOTIJEVIC, M RAJKOVIC, V |
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STASIC, J DIMCIC, B VILOTIJEVIC, M RAJKOVIC, V |
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| doi_str |
10.1007/s12034-011-0102-8 |
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2024-07-03T22:21:42.893Z |
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| score |
7.402261 |