本研究利用霍普金森試驗機(split-Hopkinson pressure bar, SHPB)探討可銲性和非可銲性之鋁鈧合金的動態變形行為。變形之應變速率範圍為：1.2×103s-1到5.9×103s-1；在各應變速率下，變形之溫度分別為-100℃, 25℃及300℃。藉以探討應變速率及溫度對兩種鋁鈧合金之動態機械反應的影響；並利用SEM及TEM技術分析兩種鋁鈧合金之破壞形貌及微觀組織變化情形。研究結果顯示兩種鋁鈧合金的塑流應力隨、加工硬化率及應變速率敏感性係數皆隨著應變速率增加而增加，但卻隨溫度增加而減少。且非可銲性之鋁鈧合金之塑流應力、加工硬化率及應變速率皆高於可銲性鋁鈧合金。而兩種鋁鈧合金變形時的熱活化體積及熱活化能(∆G*)，皆隨溫度的上升及應變速率下降而增加。此外，Zerilli-Armstrong FCC模式之統制方程式可準確地用來描述兩種鋁鈧合金動態塑性變形行為，其誤差值皆在5％之內。SEM的破壞形貌分析結果顯示，兩種鋁鈧合金破壞表面皆存在韌窩(dimple-like)組織的破壞形貌，屬韌性破壞的類別。同時比較兩種鋁鈧合金破壞形貌發現，非可銲性的鋁鈧合金破壞表面的韌窩形狀較可銲性鋁鈧合金來得平坦且稀疏，顯示可銲性鋁鈧合金的延性較非可銲性鋁鈧合金較佳。微觀TEM之觀察發現，兩種鋁鈧合金都有Al3Sc析出物析出在基地及晶界處，並造成差排在析出物附近累積；這些Al3Sc析出物可以阻擋差排的運動，並形成強化的重要因素。從差排結構分析中，可發現兩種鋁鈧合金之差排密度皆隨應變速率之增加而增加，但卻隨溫度上升而減少。此外，非可銲性鋁鈧合金之差排密度在各種實驗條件下皆高於可銲性鋁鈧合金，其對應之差排胞尺寸卻小於可銲性鋁鈧合金，可再度印證非可銲性鋁鈧合金較可銲性鋁鈧合金有較高的塑流阻抗。

This thesis utilizes a compressive split-Hopkinson pressure bar to investigate the dynamic deformation behaviours of two weldable and unweldable Al-Sc alloys at strain rates ranging from 1.2×103s-1 to 5.9×103s-1 and temperatures of –100 , 25 and 300 , respectively. The fracture features and microstructures of the impacted specimens are examined using scanning electron microscopy and transmission electron microscopy, respectively. The stress-strain relationships indicate that for both alloys, the flow stress, work hardening rate and strain rate sensitivity increase with increasing strain rate, but decrease with increasing temperature. Moreover, the flow stress, work hardening rate and strain rate sensitivity are higher in the unweldable Al-Sc alloy than in the weldable alloy. In both alloys, the activation volume and activation energy increase as the temperature increases or the strain rate decreases. Additionally, the fracture strain reduces with increasing strain rate and decreasing temperature. In describing the plastic deformation behaviour of the two Al-Sc alloys using the Zerilli-Armstrong fcc constitutive model, the error between the predicted flow stress and the measured stress is found to be less than 5%. The SEM observations reveal that the surfaces of the fractured specimens are characterised by transgranular dimple-like features, which are indicative of a ductile fracture mode. The dimple-like structures on the fracture surfaces of the unweldable Al-Sc alloy are shallower than those on the fracture surfaces of the weldable Al-Sc alloy, which indicates that the weldable Al-Sc alloy has a better ductility than the unweldable Al-Sc alloy. The TEM images show that the microstructures of the two alloys contain a random dispersion of fine Al3Sc precipitates within the matrix and an accumulation of relatively coarse Al3Sc precipitates at the grain boundaries. These particles prevent dislocation motion, and therefore prompt a significant strengthening effect. The TEM observations also reveal that in both alloys, the dislocation density increases with increasing strain rate, but decreases with increasing temperature. Furthermore, it is found that the dislocation density of the unweldable Al-Sc alloy is higher than that of the weldable Al-Sc alloy. In other words, the dislocation cells in the unweldable Al-Sc alloy are smaller than those in the weldable Al-Sc alloy. Thus, it is inferred that the unweldable Al-Sc alloy has a higher flow stress than the weldable Al-Sc alloy.

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