臺灣博碩士論文加值系統

本研究以Zr56Cu24Al9Ni7Ag4之非晶質合金為基材，再以不同比例之鈮、鉬
等元素替代銀元素，並以鈷元素替代鎳元素，以製備出Zr56Cu24Al9Ni7Nb4-xAgx
、Zr56Cu24Al9Ni7Mo4-xAgx與Zr56Cu24Al9Co7Mo4-xAgx等 14 種非晶質合金，並
探討各材料之玻璃形成能力、機械性質(變形行為)與微觀組織。首先以 X-ray 繞
射分析確認材料為非晶結構，再以 DSC 熱性質分析探討材料之玻璃形成能力；
機械性質則是分別以低應變速率的靜態壓縮實驗與高應變速率的動態撞擊實驗
進行測試，靜態壓縮實驗將萬能材料試驗機 MTS 以1 × 10^-1s-1、1 × 10^-2s-1與
1 × 10^-3s-1三種應變速率進行實驗，動態撞擊實驗則採用霍普金森桿以3 ×10^3s-1、4 ×10^3s-1與5 ×10^3s-1等三種應變速率進行，最後再透過 SEM 觀察上
述 6 種應變速率下材料之破斷表面與側面之微觀形貌。
可經由 XRD 的結果看出，除了Zr56Cu24Al9Co7Mo4有產生Co7Mo6之金屬間
化合物以外，其他材料皆在???? = 38~39°處有一寬廣之衍射峰，均為非晶結構。而
在各系列材料中添加 1%或 4%銀元素之材料的衍射峰強度較低，表示具有較強
的玻璃形成能力。
可以從 DSC 熱性值分析之結果看出，適當的添加 1%或 4%的銀元素時，能
有效增加△Tx 值至 62.1K，Trg 值能有效增加至 0.5884，而 γ 值能增加至 0.395，
與 XRD 圖相互比較後可發現 γ 值較高的材料對應的衍射峰強度較低，由此可知，
γ 值為判斷此實驗之玻璃形成能力的主要依據。
從機械性質之實驗可以觀察到，Zr56Cu24Al9Ni7Ag4有著最大的破壞應力與
最高的極限應變量；在所有系列中，極限應變量會銀含量上升而隨之增加；應變
速率敏感性係數會隨著應變速率上升而隨之增加；而 Zr56Cu24Al9Ni7Mo4有著
最高的應變速率敏感性係數，表示此材料之破壞應力值較容易受應變與應變速率
影響。
而從SEM的結果可以觀察到，大部分的材料在破裂後形成魚鱗狀韌窩組織，
隨著銀含量提升，魚鱗狀韌窩組織的邊界由平滑工整逐漸變成半融化的狀態，而
隨著應變速率提升，韌窩組織的面積也逐漸增加。在Zr56Cu24Al9Co7Mo4-xAgx系
列中，於高應變速率時除了銀含量為 4%的材料外，其餘的材料皆呈現脆性破壞。

In this study, I use amorphous alloy of Zr56Cu24Al9Ni7Ag4 as the base material, then, replace the Ag element with elements such as Nb and Mo in different proportions, and change Ni with Co in order to prepare 14 kinds of amorphous alloys such as Zr56Cu24Al9Ni7Nb4-xAgx,Zr56Cu24Al9Ni7Mo4-xAgx and Zr56Cu24Al9Co7Mo4-xAgx alloys. And discuss the glass forming ability, mechanical properties (deformation behavior) and microstructure of each material. (on the mechanical property, glass forming ability (GFA) , vickers hardness and SEM image of the Zr-based bulk metallic glasses(BMGs) alloys were investigated .) First, X-ray diffraction analysis is used to confirm that the material is an amorphous alloy, and then DSC thermal property analysis is used to explore the glass forming ability(GFA) of the Zr-based BMGs. The mechanical properties are tested by static compression experiment with low strain rate and dynamic impact experiment with high strain rate. The static compression experiment uses the universal material testing machine MTS to experiment with three strain rates of 1 × 10^-1s-1、1 × 10^-2s-1 and 1 × 10^-3s-1. The dynamic impact experiment uses a Hopkinson bar with three strain rates of 3 ×10^3s-1、4 ×10^3s-1 and 5 ×10^3s-1. Finally, observe the micro morphology of the fractured surface and side surface of the material under the above 6 strain rates through SEM.
It can be seen from the XRD results that, except for Zr56Cu24Al9Co7Mo4 which produces Co7Mo6 intermetallic compounds, all other materials have a broad diffraction peak at θ=38~39°, all of which are amorphous. The diffraction peak intensity of materials with 1% or 4% Ag added to each series of materials is lower, indicating that it has strong glass forming ability.
It can be seen from the results of the DSC thermal value analysis that when appropriate 1% or 4% of Ag is added, the △Tx value can be effectively increased to 62.1K, the Trg value can be effectively increased to 0.5884, and the γ value can be increased to 0.395. After comparing with the XRD pattern, it can be found that the diffraction peak intensity of the material with the higher γ value is lower. It can be seen that the γ value is the main basis for judging the glass forming ability of this experiment.
From the experiment of mechanical properties, it can be observed that Zr56Cu24Al9Ni7Ag4 has the largest failure stress and the highest limit strain. In all series, the limit strain will increase with the increase of silver content. The strain rate sensitivity factor will increase as the strain rate rises. And Zr56Cu24Al9Ni7Mo4 has the highest strain rate sensitivity coefficient, indicating that the failure stress value of this material is more susceptible to strain and strain rate.
From the results of SEM, it can be observed that most of the materials form scaly dimple tissue after rupture. As the silver content increases, the boundary of the scaly dimple tissue gradually changes from smooth and neat to a semi-melted state, and as the strain rate increases, the area of the dimple tissue gradually increases. In the Zr56Cu24Al9Co7Mo4-xAgxseries, except for the material with 4% silver content at high strain rates, all other materials exhibit brittle failure.

目錄
第一章 緒論 1
1-1.前言 1
1-2.研究動機 2
第二章 實驗原理與文獻回顧 4
2-1.非晶質合金 4
2-1-1.非晶質合金概述 4
2-1-2.非晶質材料之發展歷程 4
2-1-3.非晶質合金之性質 7
2-1-4.形成非晶質合金之法則 10
2-1-4-1.三大經驗法則 10
2-1-4-2.非晶質合金之玻璃形成能力 12
2-1-5.非晶質合金的製備方法 13
2-1-5-1.急冷法 13
2-1-5-2.固態反應法 16
2-1-6.各種非金質合金系列[23] 17
2-1-7.非晶質合金之應用 17
2-2.塑性變形之機械測試類別 18
1.靜態或極低之應變速率範圍(ε＜10-4s-1) 18
2.低、中速之應變速率範圍(10-4s-1＜ε＜〖10〗^2 s-1) 19
3.高速之應變速率範圍(〖10〗^2 s-1＜ε＜5×〖10〗^3 s-1) 19
4.極高速之應變速率範圍(5×〖10〗^3-1＜ε) 19
2-3.材料塑性變形之特性 20
1.擴散機構(DiffusionControlled Mechanisms) 20
2.恆溫變形機構(AthermalMechanisms) 20
3.熱活化機構(Thermal Mechanisms) 20
4.差排黏滯機構(Dislocation-DragcontrolledMechanisms) 20
第I區：恆溫機構(Athermal Mechanisms) 21
第Ⅱ區：熱活化機構(Thermal Activation Mechanisms) 21
第Ⅲ區：差排黏滯機構(Viscous Drag Mechanisms) 22
2-4.一維傳波理論 22
2-5.霍普金森桿原理 24
1.入射波(Incident Wave) 24
2.反射波(Refelected Wave) 24
3.穿透波(Transmitted Wave) 24
第三章 實驗方法與步驟 50
3-1.實驗流程 50
3-2.實驗儀器與設備 51
3-2-1.真空電弧熔煉爐 51
3-2-2.慢速切割機 51
3-2-3.超音波震盪機 52
3-2-4.多功能X光繞射儀 (X-Ray Diffraction ,XRD) 52
3-2-5.高溫示差掃描量熱儀(HT-DSC) 52
3-2-6.萬能材料試驗機 53
3-2-7.霍普金森動態撞擊試驗機(SHPB) 53
3-2-8.訊號處理裝置 53
3-2-9.掃描式電子顯微鏡(SEM) 54
3-2-10數位式顯微硬度試驗機 54
第四章 實驗結果與討論 62
4-1.X-ray繞射分析 62
4-2.DSC熱性質分析 63
4-3.應力-應變曲線圖 65
4-3-1.靜態壓縮試驗 65
4-3-2.動態撞擊實驗 66
4-4.應變速率敏感性係數 67
4-4-1.靜態壓縮試驗之應變速率敏感性係數 68
4-4-2.動態撞擊試驗之應變速率敏感性係數 69
4-5. SEM破壞形貌 70
4-5-1.靜態壓縮實驗 70
4-5-2.動態撞擊實驗 71
4-6.顯微維氏硬度 72
第五章 結論 209
一、 X光繞射分析 209
二、 DSC熱性質分析 209
三、 應力-應變曲線 209
四、 應變速率敏感性係數 210
五、 SEM表面形貌 210
參考文獻 212

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