本研究有鑑於Al-Co-Cr-Cu-Fe-Ni高熵合金系統中Cu元素大量偏析於樹枝間相且降低合金高溫強度的缺點，乃針對不含Cu的Al-Co-Cr-Fe-Ni高熵合金系統作研究。由於Al與過渡元素有較強的鍵結，對微結構及機械性質有明顯的影響，故本研究改變合金系統中的Al含量，以探討Al元素對AlxCoCrFeNi高熵合金系統微結構與機械性質的影響，同時藉由高溫XRD、DSC熱分析與SEM及TEM相鑑定，研究合金高溫相變化機制，並繪製AlxCoCrFeNi高熵合金系統之相圖。此外，本研究利用高溫硬度機對此合金系統在高溫下的變形行為加以探討。
常溫下鑄態之AlxCoCrFeNi合金隨Al元素之添加，晶體結構會由FCC轉為FCC＋BCC再轉為BCC。BCC結構的形成為合金硬化之主要因素。鑄態合金中之BCC相會藉由spinodal分解機構形成奈米級雙相結構。其中Al0.9CoCrFeNi合金具有最細的雙相微結構，使其具有最高硬度Hv 527。由化學成份分析顯示形成單相FCC結構之固溶體，合金中Al含量需低於11 at.%，而要形成單相BCC結構之固溶體，合金中Al含量至少高於18.4 at.%。
AlxCoCrFeNi合金巨觀凝固組織隨Al添加量增加，由平面成長之晶粒結構轉變成柱狀之胞狀結構，再轉變成柱狀之樹枝狀結構，然後再轉變成具有針片狀組織的等軸晶粒結構、樹枝狀之等軸晶粒結構，此係由於Al含量增加，造成CoCrFeNi合金凝固時固液界面前緣液相之溫度梯度降低或組成過冷度增加所致。
Al0–Al0.3 (FCC), Al0.5–Al0.7 (FCC＋BCC) and Al1.5–Al1.8 (BCC)合金從室溫到熔點均保持相同的晶體結構。Al0.9–Al1.2合金在870 K以下為spinodal BCC+B2結構，約870 K會發生BCC轉變成FCC之相變化，然後約在927 K析出σ相並與富Fe、Cr的FCC相連接。σ相的溶解溫度約為1235 K，1235 K 以上為B2＋FCC 雙相結構。
AlxCoCrFeNi合金的高溫硬度轉換溫度（TT）範圍為810–930 K，Al0.5合金呈現最高的TT/Tm值。高於TT溫度的高溫區間，Al0–Al0.3合金具有最低的軟化係數，而Al0.9及Al1.0合金則具有最大的軟化係數，不過在973–1073 K溫度區間，這兩組合金會因σ相的析出而再硬化。
由壓痕潛變試驗顯示，具有FCC單相的Al0.3合金主要變形機構為差排滑移，對於x ≥ 0.5的合金系統，在低於高溫硬度轉換溫度的低溫區間，合金的主要變形機構為差排滑移，而在高於高溫硬度轉換溫度的高溫區間，合金的主要變形機構為差排滑移與爬移（潛變）。

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