Morphology and Kinetics of Interfacial Layer Formation during Continuous Hot-Dip Galvanizing and Galvannealing
Abstract A galvanizing simulator with rapid spot cooling was used to obtain a well-characterized reaction times as short as 2 seconds in order to study the short-time microstructural development and kinetics of the galvanizing and galvannealing interfacial reaction layer. It was determined that the...
Ausführliche Beschreibung
Gespeichert in:
| Autor*in: |
Chen, L. [verfasserIn] |
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| Format: |
E-Artikel |
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| Sprache: |
Englisch |
| Erschienen: |
2008 |
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| Schlagwörter: |
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| Anmerkung: |
© The Minerals, Metals & Materials Society and ASM International 2008 |
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| Übergeordnetes Werk: |
Enthalten in: Metallurgical and materials transactions - Boston : Springer, 1975, 39(2008), 9 vom: 22. Mai |
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| Übergeordnetes Werk: |
volume:39 ; year:2008 ; number:9 ; day:22 ; month:05 |
| Links: |
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| DOI / URN: |
10.1007/s11661-008-9552-z |
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| Katalog-ID: |
SPR021370354 |
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| 100 | 1 | |a Chen, L. |e verfasserin |4 aut | |
| 245 | 1 | 0 | |a Morphology and Kinetics of Interfacial Layer Formation during Continuous Hot-Dip Galvanizing and Galvannealing |
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| 520 | |a Abstract A galvanizing simulator with rapid spot cooling was used to obtain a well-characterized reaction times as short as 2 seconds in order to study the short-time microstructural development and kinetics of the galvanizing and galvannealing interfacial reaction layer. It was determined that the incubation and nucleation events of the interfacial layer formation were completed by the 2-second reaction time in all cases. For a 0.20 wt pct dissolved Al bath, $ FeAl_{3} $ nucleates and grows during the initial stages of interfacial layer formation followed by $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ formation by diffusion-controlled transformation and growth. The final microstructure of the interfacial layer consisted of $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ in a two-layer arrangement comprising a fine-grained, compact lower layer with a coarser, noncompact upper layer. The Al content of the interfacial layer increased with reaction time and reaction temperature. Both of the Fe-Al phases formed exhibited a strong preferential crystallographic orientation with respect to the substrate surface. The evolution of the interfacial layer formed in a 0.13 wt pct dissolved Al bath was the result of competing processes. Fe-Al phases formed and grew during the reaction times explored, per the preceding mechanism. However, Fe-Zn phases also nucleated and grew during the reaction times explored via the process of inhibition breakdown, with these phases dominating the interfacial layer microstructures at longer reaction times. In this case, the Al content of the interfacial layer increased for all reaction times explored, but decreased with increasing reaction temperature, due to the more rapid initiation of inhibition breakdown. A model to describe the interfacial layer growth kinetics as a function of reaction time, bath temperature, and inhibition layer microstructure for the case of the 0.20 wt pct dissolved Al bath was proposed. It indicated that the development of microstructure of the interfacial layer had significant influence on the effective diffusion coefficient and growth rate of this layer. | ||
| 650 | 4 | |a Interfacial Layer |7 (dpeaa)DE-He213 | |
| 650 | 4 | |a Immersion Time |7 (dpeaa)DE-He213 | |
| 650 | 4 | |a Inhibition Layer |7 (dpeaa)DE-He213 | |
| 650 | 4 | |a Zinc Bath |7 (dpeaa)DE-He213 | |
| 650 | 4 | |a Spot Cool |7 (dpeaa)DE-He213 | |
| 700 | 1 | |a Fourmentin, R. |4 aut | |
| 700 | 1 | |a Mc Dermid, J.R. |4 aut | |
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10.1007/s11661-008-9552-z doi (DE-627)SPR021370354 (SPR)s11661-008-9552-z-e DE-627 ger DE-627 rakwb eng Chen, L. verfasserin aut Morphology and Kinetics of Interfacial Layer Formation during Continuous Hot-Dip Galvanizing and Galvannealing 2008 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Minerals, Metals & Materials Society and ASM International 2008 Abstract A galvanizing simulator with rapid spot cooling was used to obtain a well-characterized reaction times as short as 2 seconds in order to study the short-time microstructural development and kinetics of the galvanizing and galvannealing interfacial reaction layer. It was determined that the incubation and nucleation events of the interfacial layer formation were completed by the 2-second reaction time in all cases. For a 0.20 wt pct dissolved Al bath, $ FeAl_{3} $ nucleates and grows during the initial stages of interfacial layer formation followed by $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ formation by diffusion-controlled transformation and growth. The final microstructure of the interfacial layer consisted of $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ in a two-layer arrangement comprising a fine-grained, compact lower layer with a coarser, noncompact upper layer. The Al content of the interfacial layer increased with reaction time and reaction temperature. Both of the Fe-Al phases formed exhibited a strong preferential crystallographic orientation with respect to the substrate surface. The evolution of the interfacial layer formed in a 0.13 wt pct dissolved Al bath was the result of competing processes. Fe-Al phases formed and grew during the reaction times explored, per the preceding mechanism. However, Fe-Zn phases also nucleated and grew during the reaction times explored via the process of inhibition breakdown, with these phases dominating the interfacial layer microstructures at longer reaction times. In this case, the Al content of the interfacial layer increased for all reaction times explored, but decreased with increasing reaction temperature, due to the more rapid initiation of inhibition breakdown. A model to describe the interfacial layer growth kinetics as a function of reaction time, bath temperature, and inhibition layer microstructure for the case of the 0.20 wt pct dissolved Al bath was proposed. It indicated that the development of microstructure of the interfacial layer had significant influence on the effective diffusion coefficient and growth rate of this layer. Interfacial Layer (dpeaa)DE-He213 Immersion Time (dpeaa)DE-He213 Inhibition Layer (dpeaa)DE-He213 Zinc Bath (dpeaa)DE-He213 Spot Cool (dpeaa)DE-He213 Fourmentin, R. aut Mc Dermid, J.R. aut Enthalten in Metallurgical and materials transactions Boston : Springer, 1975 39(2008), 9 vom: 22. Mai (DE-627)325571996 (DE-600)2037517-7 1543-1940 nnns volume:39 year:2008 number:9 day:22 month:05 https://dx.doi.org/10.1007/s11661-008-9552-z 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_101 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_266 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_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_4328 GBV_ILN_4333 GBV_ILN_4334 GBV_ILN_4335 GBV_ILN_4336 GBV_ILN_4338 GBV_ILN_4393 GBV_ILN_4700 AR 39 2008 9 22 05 |
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10.1007/s11661-008-9552-z doi (DE-627)SPR021370354 (SPR)s11661-008-9552-z-e DE-627 ger DE-627 rakwb eng Chen, L. verfasserin aut Morphology and Kinetics of Interfacial Layer Formation during Continuous Hot-Dip Galvanizing and Galvannealing 2008 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Minerals, Metals & Materials Society and ASM International 2008 Abstract A galvanizing simulator with rapid spot cooling was used to obtain a well-characterized reaction times as short as 2 seconds in order to study the short-time microstructural development and kinetics of the galvanizing and galvannealing interfacial reaction layer. It was determined that the incubation and nucleation events of the interfacial layer formation were completed by the 2-second reaction time in all cases. For a 0.20 wt pct dissolved Al bath, $ FeAl_{3} $ nucleates and grows during the initial stages of interfacial layer formation followed by $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ formation by diffusion-controlled transformation and growth. The final microstructure of the interfacial layer consisted of $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ in a two-layer arrangement comprising a fine-grained, compact lower layer with a coarser, noncompact upper layer. The Al content of the interfacial layer increased with reaction time and reaction temperature. Both of the Fe-Al phases formed exhibited a strong preferential crystallographic orientation with respect to the substrate surface. The evolution of the interfacial layer formed in a 0.13 wt pct dissolved Al bath was the result of competing processes. Fe-Al phases formed and grew during the reaction times explored, per the preceding mechanism. However, Fe-Zn phases also nucleated and grew during the reaction times explored via the process of inhibition breakdown, with these phases dominating the interfacial layer microstructures at longer reaction times. In this case, the Al content of the interfacial layer increased for all reaction times explored, but decreased with increasing reaction temperature, due to the more rapid initiation of inhibition breakdown. A model to describe the interfacial layer growth kinetics as a function of reaction time, bath temperature, and inhibition layer microstructure for the case of the 0.20 wt pct dissolved Al bath was proposed. It indicated that the development of microstructure of the interfacial layer had significant influence on the effective diffusion coefficient and growth rate of this layer. Interfacial Layer (dpeaa)DE-He213 Immersion Time (dpeaa)DE-He213 Inhibition Layer (dpeaa)DE-He213 Zinc Bath (dpeaa)DE-He213 Spot Cool (dpeaa)DE-He213 Fourmentin, R. aut Mc Dermid, J.R. aut Enthalten in Metallurgical and materials transactions Boston : Springer, 1975 39(2008), 9 vom: 22. Mai (DE-627)325571996 (DE-600)2037517-7 1543-1940 nnns volume:39 year:2008 number:9 day:22 month:05 https://dx.doi.org/10.1007/s11661-008-9552-z 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_101 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_266 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_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_4328 GBV_ILN_4333 GBV_ILN_4334 GBV_ILN_4335 GBV_ILN_4336 GBV_ILN_4338 GBV_ILN_4393 GBV_ILN_4700 AR 39 2008 9 22 05 |
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10.1007/s11661-008-9552-z doi (DE-627)SPR021370354 (SPR)s11661-008-9552-z-e DE-627 ger DE-627 rakwb eng Chen, L. verfasserin aut Morphology and Kinetics of Interfacial Layer Formation during Continuous Hot-Dip Galvanizing and Galvannealing 2008 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Minerals, Metals & Materials Society and ASM International 2008 Abstract A galvanizing simulator with rapid spot cooling was used to obtain a well-characterized reaction times as short as 2 seconds in order to study the short-time microstructural development and kinetics of the galvanizing and galvannealing interfacial reaction layer. It was determined that the incubation and nucleation events of the interfacial layer formation were completed by the 2-second reaction time in all cases. For a 0.20 wt pct dissolved Al bath, $ FeAl_{3} $ nucleates and grows during the initial stages of interfacial layer formation followed by $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ formation by diffusion-controlled transformation and growth. The final microstructure of the interfacial layer consisted of $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ in a two-layer arrangement comprising a fine-grained, compact lower layer with a coarser, noncompact upper layer. The Al content of the interfacial layer increased with reaction time and reaction temperature. Both of the Fe-Al phases formed exhibited a strong preferential crystallographic orientation with respect to the substrate surface. The evolution of the interfacial layer formed in a 0.13 wt pct dissolved Al bath was the result of competing processes. Fe-Al phases formed and grew during the reaction times explored, per the preceding mechanism. However, Fe-Zn phases also nucleated and grew during the reaction times explored via the process of inhibition breakdown, with these phases dominating the interfacial layer microstructures at longer reaction times. In this case, the Al content of the interfacial layer increased for all reaction times explored, but decreased with increasing reaction temperature, due to the more rapid initiation of inhibition breakdown. A model to describe the interfacial layer growth kinetics as a function of reaction time, bath temperature, and inhibition layer microstructure for the case of the 0.20 wt pct dissolved Al bath was proposed. It indicated that the development of microstructure of the interfacial layer had significant influence on the effective diffusion coefficient and growth rate of this layer. Interfacial Layer (dpeaa)DE-He213 Immersion Time (dpeaa)DE-He213 Inhibition Layer (dpeaa)DE-He213 Zinc Bath (dpeaa)DE-He213 Spot Cool (dpeaa)DE-He213 Fourmentin, R. aut Mc Dermid, J.R. aut Enthalten in Metallurgical and materials transactions Boston : Springer, 1975 39(2008), 9 vom: 22. Mai (DE-627)325571996 (DE-600)2037517-7 1543-1940 nnns volume:39 year:2008 number:9 day:22 month:05 https://dx.doi.org/10.1007/s11661-008-9552-z 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_101 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_266 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_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_4328 GBV_ILN_4333 GBV_ILN_4334 GBV_ILN_4335 GBV_ILN_4336 GBV_ILN_4338 GBV_ILN_4393 GBV_ILN_4700 AR 39 2008 9 22 05 |
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10.1007/s11661-008-9552-z doi (DE-627)SPR021370354 (SPR)s11661-008-9552-z-e DE-627 ger DE-627 rakwb eng Chen, L. verfasserin aut Morphology and Kinetics of Interfacial Layer Formation during Continuous Hot-Dip Galvanizing and Galvannealing 2008 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Minerals, Metals & Materials Society and ASM International 2008 Abstract A galvanizing simulator with rapid spot cooling was used to obtain a well-characterized reaction times as short as 2 seconds in order to study the short-time microstructural development and kinetics of the galvanizing and galvannealing interfacial reaction layer. It was determined that the incubation and nucleation events of the interfacial layer formation were completed by the 2-second reaction time in all cases. For a 0.20 wt pct dissolved Al bath, $ FeAl_{3} $ nucleates and grows during the initial stages of interfacial layer formation followed by $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ formation by diffusion-controlled transformation and growth. The final microstructure of the interfacial layer consisted of $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ in a two-layer arrangement comprising a fine-grained, compact lower layer with a coarser, noncompact upper layer. The Al content of the interfacial layer increased with reaction time and reaction temperature. Both of the Fe-Al phases formed exhibited a strong preferential crystallographic orientation with respect to the substrate surface. The evolution of the interfacial layer formed in a 0.13 wt pct dissolved Al bath was the result of competing processes. Fe-Al phases formed and grew during the reaction times explored, per the preceding mechanism. However, Fe-Zn phases also nucleated and grew during the reaction times explored via the process of inhibition breakdown, with these phases dominating the interfacial layer microstructures at longer reaction times. In this case, the Al content of the interfacial layer increased for all reaction times explored, but decreased with increasing reaction temperature, due to the more rapid initiation of inhibition breakdown. A model to describe the interfacial layer growth kinetics as a function of reaction time, bath temperature, and inhibition layer microstructure for the case of the 0.20 wt pct dissolved Al bath was proposed. It indicated that the development of microstructure of the interfacial layer had significant influence on the effective diffusion coefficient and growth rate of this layer. Interfacial Layer (dpeaa)DE-He213 Immersion Time (dpeaa)DE-He213 Inhibition Layer (dpeaa)DE-He213 Zinc Bath (dpeaa)DE-He213 Spot Cool (dpeaa)DE-He213 Fourmentin, R. aut Mc Dermid, J.R. aut Enthalten in Metallurgical and materials transactions Boston : Springer, 1975 39(2008), 9 vom: 22. Mai (DE-627)325571996 (DE-600)2037517-7 1543-1940 nnns volume:39 year:2008 number:9 day:22 month:05 https://dx.doi.org/10.1007/s11661-008-9552-z 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_101 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_266 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_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_4328 GBV_ILN_4333 GBV_ILN_4334 GBV_ILN_4335 GBV_ILN_4336 GBV_ILN_4338 GBV_ILN_4393 GBV_ILN_4700 AR 39 2008 9 22 05 |
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10.1007/s11661-008-9552-z doi (DE-627)SPR021370354 (SPR)s11661-008-9552-z-e DE-627 ger DE-627 rakwb eng Chen, L. verfasserin aut Morphology and Kinetics of Interfacial Layer Formation during Continuous Hot-Dip Galvanizing and Galvannealing 2008 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Minerals, Metals & Materials Society and ASM International 2008 Abstract A galvanizing simulator with rapid spot cooling was used to obtain a well-characterized reaction times as short as 2 seconds in order to study the short-time microstructural development and kinetics of the galvanizing and galvannealing interfacial reaction layer. It was determined that the incubation and nucleation events of the interfacial layer formation were completed by the 2-second reaction time in all cases. For a 0.20 wt pct dissolved Al bath, $ FeAl_{3} $ nucleates and grows during the initial stages of interfacial layer formation followed by $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ formation by diffusion-controlled transformation and growth. The final microstructure of the interfacial layer consisted of $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ in a two-layer arrangement comprising a fine-grained, compact lower layer with a coarser, noncompact upper layer. The Al content of the interfacial layer increased with reaction time and reaction temperature. Both of the Fe-Al phases formed exhibited a strong preferential crystallographic orientation with respect to the substrate surface. The evolution of the interfacial layer formed in a 0.13 wt pct dissolved Al bath was the result of competing processes. Fe-Al phases formed and grew during the reaction times explored, per the preceding mechanism. However, Fe-Zn phases also nucleated and grew during the reaction times explored via the process of inhibition breakdown, with these phases dominating the interfacial layer microstructures at longer reaction times. In this case, the Al content of the interfacial layer increased for all reaction times explored, but decreased with increasing reaction temperature, due to the more rapid initiation of inhibition breakdown. A model to describe the interfacial layer growth kinetics as a function of reaction time, bath temperature, and inhibition layer microstructure for the case of the 0.20 wt pct dissolved Al bath was proposed. It indicated that the development of microstructure of the interfacial layer had significant influence on the effective diffusion coefficient and growth rate of this layer. Interfacial Layer (dpeaa)DE-He213 Immersion Time (dpeaa)DE-He213 Inhibition Layer (dpeaa)DE-He213 Zinc Bath (dpeaa)DE-He213 Spot Cool (dpeaa)DE-He213 Fourmentin, R. aut Mc Dermid, J.R. aut Enthalten in Metallurgical and materials transactions Boston : Springer, 1975 39(2008), 9 vom: 22. Mai (DE-627)325571996 (DE-600)2037517-7 1543-1940 nnns volume:39 year:2008 number:9 day:22 month:05 https://dx.doi.org/10.1007/s11661-008-9552-z 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_101 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_266 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_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_4328 GBV_ILN_4333 GBV_ILN_4334 GBV_ILN_4335 GBV_ILN_4336 GBV_ILN_4338 GBV_ILN_4393 GBV_ILN_4700 AR 39 2008 9 22 05 |
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English |
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Enthalten in Metallurgical and materials transactions 39(2008), 9 vom: 22. Mai volume:39 year:2008 number:9 day:22 month:05 |
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Enthalten in Metallurgical and materials transactions 39(2008), 9 vom: 22. Mai volume:39 year:2008 number:9 day:22 month:05 |
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Interfacial Layer Immersion Time Inhibition Layer Zinc Bath Spot Cool |
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Metallurgical and materials transactions |
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Chen, L. @@aut@@ Fourmentin, R. @@aut@@ Mc Dermid, J.R. @@aut@@ |
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2008-05-22T00:00:00Z |
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It was determined that the incubation and nucleation events of the interfacial layer formation were completed by the 2-second reaction time in all cases. For a 0.20 wt pct dissolved Al bath, $ FeAl_{3} $ nucleates and grows during the initial stages of interfacial layer formation followed by $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ formation by diffusion-controlled transformation and growth. The final microstructure of the interfacial layer consisted of $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ in a two-layer arrangement comprising a fine-grained, compact lower layer with a coarser, noncompact upper layer. The Al content of the interfacial layer increased with reaction time and reaction temperature. Both of the Fe-Al phases formed exhibited a strong preferential crystallographic orientation with respect to the substrate surface. The evolution of the interfacial layer formed in a 0.13 wt pct dissolved Al bath was the result of competing processes. Fe-Al phases formed and grew during the reaction times explored, per the preceding mechanism. However, Fe-Zn phases also nucleated and grew during the reaction times explored via the process of inhibition breakdown, with these phases dominating the interfacial layer microstructures at longer reaction times. In this case, the Al content of the interfacial layer increased for all reaction times explored, but decreased with increasing reaction temperature, due to the more rapid initiation of inhibition breakdown. A model to describe the interfacial layer growth kinetics as a function of reaction time, bath temperature, and inhibition layer microstructure for the case of the 0.20 wt pct dissolved Al bath was proposed. 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Chen, L. |
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Chen, L. misc Interfacial Layer misc Immersion Time misc Inhibition Layer misc Zinc Bath misc Spot Cool Morphology and Kinetics of Interfacial Layer Formation during Continuous Hot-Dip Galvanizing and Galvannealing |
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Morphology and Kinetics of Interfacial Layer Formation during Continuous Hot-Dip Galvanizing and Galvannealing Interfacial Layer (dpeaa)DE-He213 Immersion Time (dpeaa)DE-He213 Inhibition Layer (dpeaa)DE-He213 Zinc Bath (dpeaa)DE-He213 Spot Cool (dpeaa)DE-He213 |
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misc Interfacial Layer misc Immersion Time misc Inhibition Layer misc Zinc Bath misc Spot Cool |
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misc Interfacial Layer misc Immersion Time misc Inhibition Layer misc Zinc Bath misc Spot Cool |
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Morphology and Kinetics of Interfacial Layer Formation during Continuous Hot-Dip Galvanizing and Galvannealing |
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Morphology and Kinetics of Interfacial Layer Formation during Continuous Hot-Dip Galvanizing and Galvannealing |
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Chen, L. |
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morphology and kinetics of interfacial layer formation during continuous hot-dip galvanizing and galvannealing |
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Morphology and Kinetics of Interfacial Layer Formation during Continuous Hot-Dip Galvanizing and Galvannealing |
| abstract |
Abstract A galvanizing simulator with rapid spot cooling was used to obtain a well-characterized reaction times as short as 2 seconds in order to study the short-time microstructural development and kinetics of the galvanizing and galvannealing interfacial reaction layer. It was determined that the incubation and nucleation events of the interfacial layer formation were completed by the 2-second reaction time in all cases. For a 0.20 wt pct dissolved Al bath, $ FeAl_{3} $ nucleates and grows during the initial stages of interfacial layer formation followed by $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ formation by diffusion-controlled transformation and growth. The final microstructure of the interfacial layer consisted of $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ in a two-layer arrangement comprising a fine-grained, compact lower layer with a coarser, noncompact upper layer. The Al content of the interfacial layer increased with reaction time and reaction temperature. Both of the Fe-Al phases formed exhibited a strong preferential crystallographic orientation with respect to the substrate surface. The evolution of the interfacial layer formed in a 0.13 wt pct dissolved Al bath was the result of competing processes. Fe-Al phases formed and grew during the reaction times explored, per the preceding mechanism. However, Fe-Zn phases also nucleated and grew during the reaction times explored via the process of inhibition breakdown, with these phases dominating the interfacial layer microstructures at longer reaction times. In this case, the Al content of the interfacial layer increased for all reaction times explored, but decreased with increasing reaction temperature, due to the more rapid initiation of inhibition breakdown. A model to describe the interfacial layer growth kinetics as a function of reaction time, bath temperature, and inhibition layer microstructure for the case of the 0.20 wt pct dissolved Al bath was proposed. It indicated that the development of microstructure of the interfacial layer had significant influence on the effective diffusion coefficient and growth rate of this layer. © The Minerals, Metals & Materials Society and ASM International 2008 |
| abstractGer |
Abstract A galvanizing simulator with rapid spot cooling was used to obtain a well-characterized reaction times as short as 2 seconds in order to study the short-time microstructural development and kinetics of the galvanizing and galvannealing interfacial reaction layer. It was determined that the incubation and nucleation events of the interfacial layer formation were completed by the 2-second reaction time in all cases. For a 0.20 wt pct dissolved Al bath, $ FeAl_{3} $ nucleates and grows during the initial stages of interfacial layer formation followed by $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ formation by diffusion-controlled transformation and growth. The final microstructure of the interfacial layer consisted of $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ in a two-layer arrangement comprising a fine-grained, compact lower layer with a coarser, noncompact upper layer. The Al content of the interfacial layer increased with reaction time and reaction temperature. Both of the Fe-Al phases formed exhibited a strong preferential crystallographic orientation with respect to the substrate surface. The evolution of the interfacial layer formed in a 0.13 wt pct dissolved Al bath was the result of competing processes. Fe-Al phases formed and grew during the reaction times explored, per the preceding mechanism. However, Fe-Zn phases also nucleated and grew during the reaction times explored via the process of inhibition breakdown, with these phases dominating the interfacial layer microstructures at longer reaction times. In this case, the Al content of the interfacial layer increased for all reaction times explored, but decreased with increasing reaction temperature, due to the more rapid initiation of inhibition breakdown. A model to describe the interfacial layer growth kinetics as a function of reaction time, bath temperature, and inhibition layer microstructure for the case of the 0.20 wt pct dissolved Al bath was proposed. It indicated that the development of microstructure of the interfacial layer had significant influence on the effective diffusion coefficient and growth rate of this layer. © The Minerals, Metals & Materials Society and ASM International 2008 |
| abstract_unstemmed |
Abstract A galvanizing simulator with rapid spot cooling was used to obtain a well-characterized reaction times as short as 2 seconds in order to study the short-time microstructural development and kinetics of the galvanizing and galvannealing interfacial reaction layer. It was determined that the incubation and nucleation events of the interfacial layer formation were completed by the 2-second reaction time in all cases. For a 0.20 wt pct dissolved Al bath, $ FeAl_{3} $ nucleates and grows during the initial stages of interfacial layer formation followed by $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ formation by diffusion-controlled transformation and growth. The final microstructure of the interfacial layer consisted of $ Fe_{2} %$ Al_{5} %$ Zn_{X} $ in a two-layer arrangement comprising a fine-grained, compact lower layer with a coarser, noncompact upper layer. The Al content of the interfacial layer increased with reaction time and reaction temperature. Both of the Fe-Al phases formed exhibited a strong preferential crystallographic orientation with respect to the substrate surface. The evolution of the interfacial layer formed in a 0.13 wt pct dissolved Al bath was the result of competing processes. Fe-Al phases formed and grew during the reaction times explored, per the preceding mechanism. However, Fe-Zn phases also nucleated and grew during the reaction times explored via the process of inhibition breakdown, with these phases dominating the interfacial layer microstructures at longer reaction times. In this case, the Al content of the interfacial layer increased for all reaction times explored, but decreased with increasing reaction temperature, due to the more rapid initiation of inhibition breakdown. A model to describe the interfacial layer growth kinetics as a function of reaction time, bath temperature, and inhibition layer microstructure for the case of the 0.20 wt pct dissolved Al bath was proposed. It indicated that the development of microstructure of the interfacial layer had significant influence on the effective diffusion coefficient and growth rate of this layer. © The Minerals, Metals & Materials Society and ASM International 2008 |
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| title_short |
Morphology and Kinetics of Interfacial Layer Formation during Continuous Hot-Dip Galvanizing and Galvannealing |
| url |
https://dx.doi.org/10.1007/s11661-008-9552-z |
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| author2 |
Fourmentin, R. Mc Dermid, J.R. |
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| doi_str |
10.1007/s11661-008-9552-z |
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2024-07-03T22:08:06.674Z |
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| score |
7.4005013 |