本研究在錳鋁鋼材表面預電鍍一層200 nm、1000 nm、2000 nm及3000 nm厚的鎳後，在鋁含量0.2 wt%鋅浴中進行熱浸鍍鋅，探討溫度與時間對預電鍍不同厚度鎳層的錳鋁鋼合金化反應前後的影響。完鍍試片以掃描式電子顯微鏡、場發射高解析電子微探儀及X光繞射儀分析表面形貌與鍍層結構，後續使用紅外線退火爐模擬合金化實驗，並同樣以掃描式電子顯微鏡、場發射高解析電子微探儀及X光繞射儀分析實驗後的鍍層結構。
實驗結果顯示，預鍍鎳試片在熱浸鍍鋅時，鎳鋅介面反應產物無法形成連續的阻障層阻止進一步的反應，因此合金化反應已從鎳鋅介面開始。當鎳層厚度為200 nm時，在底材與鍍層介面處形成δ-鐵鋅相，其上為T相，二者厚度佔整個鍍層厚度的三分之一，上方的三分之二厚度為純鋅與β1-鎳鋅相的混合組織。鎳層厚度為1000 nm時，介面沒有鐵鋅相的生成，而在底材介面處形成T相，其上有γ-鎳鋅相及純鋅的混合組織生成，表面也有鎳鋁相的生成。鎳層為3000 nm時，在底材介面仍有2 μm以上的鎳層殘留，其上二分之一鍍層為γ-鎳鋅相，再上方的二分之一為γ-鎳鋅相、β1-鎳鋅相及純鋅的複合組織。
合金化反應結果顯示，預鍍鎳的厚度對所生成的合金相有重要影響。鎳層厚度為1000 nm時，合金化反應初期以T相及δ-鐵鋅相為主，隨溫度上升與時間增加，在底材介面處會形成Γ-鐵鋅相，其上仍為δ-鐵鋅相及T相。鎳層厚度為2000 nm時，合金化反應初期由介面依序形成δ-鐵鋅相、T相及γ-鎳鋅相，隨溫度上升與時間增加，在底材介面處會形成Γ-鐵鋅相，其上為T相及γ-鎳鋅相；鎳層厚度為3000 nm時，合金化反應初期以γ-鎳鋅相為主，隨溫度上升與時間增加，鍍層仍以γ-鎳鋅相為主，但近表面的鍍層中鋁的固溶量增加。且合金化鍍層表面形成的鎳鋁相主要是由鋅浴中的鋁與鎳層反應生成。

In this study, a nickel layer of 200 nm - 3000 nm thick was electrodeposited on the surface of a cold-rolled 6 wt% Mn-3wt% Al steel. The coated steel was then hot dip galvanized in a zinc bath containing 0.2 wt% of aluminum. The effect of the Ni thickness on the microstructures of the Zn coating before and after galvannealing were studied by x-ray diffraction, scanning electron microscopy and electron electron probe X-ray microanalyzer.
The experimental results showed that the interfacial reactions at the nickel-zinc interface proceeded on dipping, indicating the absence of an effective barrier layer formed at the interface. For the galvanized sample pre-coated with a nickel layer of 200 nm, a layer of δ-iron/zinc phase was formed at the interface followed by a T phase layer. On top of the T and δ-iron/zinc layers, a thick layer of Zn/β1-phase mixture was formed. For the galvanized sample pre-coated with a nickel layer of 1000 nm, no Fe-Zn phase was found at the interface. Instead, the coating is composed of a T-phase layer, a γ-nickel-zinc phase layer and a layer of Zn/γ-nickel-zinc phase mixture. At a thick nickel layer of 3000 nm, the galvanized coating consisted of a nickel layer of 2 μm thick, a γ-nickel-zinc phase layer and a Zn/γ/β1 mixture layer.
After galvannealing at 460-550 oC for 10-100 s, the alloying layer was composed of δ-Fe-Zn phase and T phase initially for the sample with a 1000 nm Ni layer. On increasing the galvannealing temperature, G Fe-Zn phase was formed at the interface. For the sample pre-coated with a 2000 nm Ni layer, the alloying layer is composed of δ-Fe-Zn, T and γ-Ni-Zn phases in sequence. The δ-Fe-Zn phase transformed to the γ-Fe-Zn phase on subsequent annealing. With increasing the Ni layer thickness to 3000 nm, the coating contained solely the γ-Ni-Zn phase no matter the annealing temperature and time. However, NiAl particles were observed on the surface.

論文審定書 i
誌謝 ii
摘要 iii
Abstract iv
總目錄 vi
表目錄 ix
圖目錄 x
第一章、前言 1
第二章、文獻回顧 3
2.1先進高強度鋼的特性與選擇性氧化 3
2.2 熱浸鍍鋅製程與反應機構 6
2.2.1 熱浸鍍鋅的防蝕原理 6
2.2.2 連續式熱浸鍍鋅製程 7
2.2.3 合金化熱處理 8
2.3 熱浸鍍鋅鍍層結構 8
2.3.1 Fe2Al5的形成機構 8
2.3.2 合金化反應 10
2.4 電鍍鎳之中錳鋼的選擇性氧化與合金化反應 11
第三章、實驗方法 14
3.1 試片準備 14
3.1.1 電鍍鎳製程 14
3.1.2 熱浸鍍鋅處理 15
3.1.3合金化退火處理 15
3.1.4橫截面試片製作 15
3.2 掃描式電子顯微鏡(Scanning electron microscopy, SEM)分析 16
3.3 場發射高解析電子微探儀(Electron Probe X-ray MicroAnalyzer, EPMA)分析 16
3.4 X光繞射儀(X-ray diffraction, XRD)分析 16
第四章、實驗結果 17
4.1完鍍試片的分析 17
4.1.1 1N200試片之分析 17
4.1.2 1N1000試片之分析 18
4.1.3 2N1000試片之分析 20
4.1.4 2N2000試片之分析 21
4.1.5 2N3000試片之分析 21
4.1.6 討論 22
4.2熱浸鍍鋅模擬器直接退火 23
4.2.1 XRD之分析 23
4.2.2 EPMA之分析 23
4.2.3 討論 24
4.3 RTA退火 25
4.3.1 R1000試片之分析 25
4.3.2 R2000試片之分析 28
4.3.3 R3000試片之分析 30
4.3.4 討論 31
4.4 綜合討論 33
4.4.1 相分析 33
4.4.2 元素擴散 33
4.4.3 應用 34
第五章、結論 36
第六章、參考文獻 37
附錄、圖表 45

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