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3.4. Impact strength
Fig. 7 shows the total impact energy of AM100 alloy and its composites as a function of fibre volume frac- tion. The impact energy required for fracture reduces rapidly with addition of ceramic reinforcements, whichis due to their inherently brittle nature. For both the al- loy and its composites, the presence of notch increases the stress concentration at the tip of the notch leading to a further reduction in the impact energy [7, 12, 21]. Fractographic evidence of the unreinforced alloy shows dominant intergranular failure (Fig. 8a). This is due to the reason that the base alloy is inherently brittle due to the presence of brittle Mg17 Al12 precipitates along the grain boundaries [12, 13]. Hence, addition of fibres would lead to the formation of these brittle precipitates at the fibre/matrix interface resulting in easy propaga- tion of cracks under impact loading. This can be ob- served from Fig. 8b, which shows a crack propagating through fibres. Such low resistance to crack propaga- tion results in very low absorption energy [12, 22] and eventually causes intense fibre breakage and fibre chop- ping (Fig. 8b).
3.4. Impact strength
Fig. 7 shows the total impact energy of AM100 alloy and its composites as a function of fibre volume frac- tion. The impact energy required for fracture reduces rapidly with addition of ceramic reinforcements, whichis due to their inherently brittle nature. For both the al- loy and its composites, the presence of notch increases the stress concentration at the tip of the notch leading to a further reduction in the impact energy [7, 12, 21]. Fractographic evidence of the unreinforced alloy shows dominant intergranular failure (Fig. 8a). This is due to the reason that the base alloy is inherently brittle due to the presence of brittle Mg17 Al12 precipitates along the grain boundaries [12, 13]. Hence, addition of fibres would lead to the formation of these brittle precipitates at the fibre/matrix interface resulting in easy propaga- tion of cracks under impact loading. This can be ob- served from Fig. 8b, which shows a crack propagating through fibres. Such low resistance to crack propaga- tion results in very low absorption energy [12, 22] and eventually causes intense fibre breakage and fibre chop- ping (Fig. 8b).
3.4.冲击强度
图7显示总冲击能量的AM100合金及复合材料的纤维体积功能数量-信息.冲击能量所需的基础上再增加骨折减少迅速与陶瓷增援时,由于其固有的全局脆性性质.见ad -对两个,何来及复合材料的缺口的存在增加了应力集中在顶端切口导致再减少冲击能量[7、12、第21条].电镜断口的证据显示晶合金失败(占主导地位的(图8a).这是由于基合金的原因是由于固有的存在脆脆Mg17沿晶界沉淀Al12[12,13].因此,添加纤维会导致形成沉淀于这些易碎的纤维/基体界面导致简单——实践propaga冲击荷载作用下裂缝.这可以从图-服务指挥.8b,表现出一裂纹光束通过纤维.这样的低阻裂效果propaga -变形吸收能量很低,22][12,最终导致强烈的纤维破碎和纤维斩萍(图8b).
图7显示总冲击能量的AM100合金及复合材料的纤维体积功能数量-信息.冲击能量所需的基础上再增加骨折减少迅速与陶瓷增援时,由于其固有的全局脆性性质.见ad -对两个,何来及复合材料的缺口的存在增加了应力集中在顶端切口导致再减少冲击能量[7、12、第21条].电镜断口的证据显示晶合金失败(占主导地位的(图8a).这是由于基合金的原因是由于固有的存在脆脆Mg17沿晶界沉淀Al12[12,13].因此,添加纤维会导致形成沉淀于这些易碎的纤维/基体界面导致简单——实践propaga冲击荷载作用下裂缝.这可以从图-服务指挥.8b,表现出一裂纹光束通过纤维.这样的低阻裂效果propaga -变形吸收能量很低,22][12,最终导致强烈的纤维破碎和纤维斩萍(图8b).