摘 要

電氣接點在開閉期間產生的電弧行為不僅影響其表面形態而且會造成嚴重的損耗。其損耗係由機械應力和熔融電橋以及電弧等因素所造成，因而損耗機制極為複雜。因此，為了避免機械應力的影響及減少無數的電弧衝擊之複雜性，而可釐清電弧與損耗機制的關係，本研究主要使用單發放電之靜態接點電蝕試驗機實驗探討脈衝電壓、電極間隙及電弧持續時間對銀基接點材料的電弧損耗特性與機制之影響。同時與動態接點試驗的相關結果互相驗證。
從電弧損耗特性的探討結果得知，在脈衝電壓32V至500V和間隙距離0.2mm至40mm條件下，可區分出放電與未放電區域之邊界，且建立電弧初始之最小脈衝電壓與間隙距離之經驗式。當脈衝電壓小於200V時，電蝕面積隨著間隙距離的增加而呈線性增加，這主要受金屬相電弧的影響。但是，當脈衝電壓大於200V時，電蝕面積會隨著間隙距離的增加到最大值之後，再逐漸減少。這是受氣相電弧的增強之影響。
從電弧損耗機制的探討結果得知，電弧放電區域可區分為金屬電橋相(B)、金屬電弧相(M)與氣相電弧相(G)等三種損耗形態。亦即，在間隙距離為0.2mm時，隨著脈衝電壓的增加，損耗的形態依序從B相經B+M混合相和M相，及M+G混合相發生變化。又依電子傳輸的模式，損耗形態的B相、B+M相和M相是由熱離放射所主導，M+G相則由熱離放射與電場放射之混合所造成的結果。當脈衝電壓500V時隨著間隙距離的增加，陽極接點表面的凹洞周圍的金屬顆粒顯現出分散飛濺和更粉末化，最後消失。此結果乃由於氣體相電弧量逐漸的增強作用所造成。
在抗熔焊能力的探討結果得知，以靜態接點試驗在脈衝電壓500V和電弧能量為增至14焦耳以上時，Ag-Ni和Ag-CdO及Ag-SnO2接點材料發生熔焊時之臨界靜態間隙距離分別為3mm、8mm及15mm。這顯示Ag-Ni接點具有最佳抗熔焊能力。另一方面，以動態接點開閉試驗在電弧能量增至10焦耳以內時，抗電弧損耗、抗熔焊能力及熔焊面積大小順序為Ag-CdO＞Ag-SnO2＞Ag-Ni接點材料。然而，當電弧能量增至14焦耳以上時，抗電弧損耗、抗熔焊能力及熔焊面積大小順序為Ag-Ni＞Ag-CdO＞Ag-SnO2接點材料，其與靜態抗熔焊試驗之結果相當一致。
此外，藉由X光繞射法、差熱分析和熱重實驗分析銀基接點材料之損耗表面可得知，當電弧能量增至10焦耳以上時Ag-CdO和Ag-SnO2混合物分別局部分解為Ag-Cd和Ag-Sn合金材料，此造成抗電弧損耗及抗熔焊能力的降低。另一方面，Ag-Ni接點表面由於NiO的分散而有助於降低接點表面的熔焊傾向，導致Ag-Ni接點材料的抗損耗及抗熔焊之能力皆優於其他銀氧化物接點材料。

Abstract
The arc behavior during the closing and opening of electrical contacts not only influences the surface morphology, but also causes the erosion of contact material. The mechanical stresses, the molten bridge, and the arc cause this erosion. Consequently, the erosion mechanism is very complex. Therefore, to avoid the influences of mechanical stresses and numerous arc striking, static-gap experiments with a single arc discharge are conducted to investigate the effects of pulse voltage, gap distance, and arc duration on the erosion characteristics and mechanism of silver based contact materials. Moreover, this experimental result is verified by the finding of the dynamic testing of electrical contacts.
The results of the erosion characteristics show that the arcing and non-arcing regions have been distinguished at the supply voltage from 32 V to 500 V and the gap distance from 0.2 mm to 40 mm. The empirical formula for the minimum pulse voltage at arc initiation in terms of gap distance is established. When the pulse voltage is smaller than 200 V, the erosion area increases with increasing gap distance due to the action of the metallic-phase arc. However, when the pulse voltage is greater than 200 V, with increasing gap distance, the erosion area increases to a maxim, and finally diminishes due to the increase in the amount of gaseous-phase arc.
The results of the erosion mechanism show that the arcing region is classified into three erosion patterns, namely, the molten metal bridge (B), metallic-phase arc (M), and gaseous-phase arc (G). At the gap distance of 0.2 mm, the erosion pattern of anode silver is varied from B, through B+M, and, M, to M+G. According to the electron transfer across triangular potential barrier, the thermionic emission causes the erosion patterns of B, B+M, and M, and mixed thermionic and field emission results in the erosion pattern of M+G. When the pulse voltage is 500 V, with increasing gap distance, the splashing of metallic particles around the anode crater becomes more dispersed, shorter with more silver powder, and finally disappeared with a little silver powder due to the influence of the gaseous-phase arc.
The results of the anti-weld ability show that when the pulse voltage is 500 V and the arc energy is grater than 14 J at the static-gap experiments, the critical gap distance to produce welding for Ag-Ni, Ag-CdO, and Ag-SnO2 is 3 mm, 8 mm, and 15 mm, respectively. This indicates Ag-Ni contact possesses the best anti-weld ability. On the other hand, the results of dynamic testing of electrical contacts show that at the arc energy less than 10 J, the anti-erosion, anti-weld ability, and the welding area are seen to increase with contact materials in the following order: Ag-CdO > Ag-SnO2 > Ag-Ni. However, when the arc energy is greater than 10 J, the anti-erosion, anti-weld ability, and the erosion area are seen to increase in the reverse order: Ag-SnO2 < Ag-CdO < Ag-Ni, which are in very good agreement with the results of static-gap experiments.
Furthermore, the erosion surface of the silver-based contact materials can be observed and analyzed by using the X-ray diffraction method (XRD), differential thermal analysis (DTA), and gravitation thermal analyzer (GTA). Results show that when the arc energy is greater than 14 J, Ag-CdO and Ag-SnO2 have been decomposed into Ag-Cd and Ag-Sn alloys, respectively, which reduce their anti-weld ability. On the other hand, the welding trend has been reduced due to the dispersion of NiO on the surface of Ag-Ni contact. Consequently, the anti-erosion and anti-weld ability for the Ag-Ni contacts are better than those of the other Ag-MeO contact materials.

總目錄

中文摘要 i
總目錄 iii
圖目錄 vi
表目錄 xi
符號說明 xii
第一章 諸論
1-1 研究動機 1
1-2 放電現象的發生與種類 4
1-3 氣體放電原理 7
1-3-1 電漿的形成 7
1-3-2 電子的放射 11
1-3-3 電弧損耗的形態 14
1-4 文獻回顧 15
1-4-1 氣體崩潰的探討 15
1-4-2 接點電弧的特性 18
1-4-3 接點材料的損耗與轉移 23
1-4-4 靜態間隙放電對接點材料的探討 26
1-4-5 接點材料的抗熔與黏著 28
1-5 本論文的研究方向 29
1-6 本論文的架構 32
第二章 靜態間隙銀接點電弧特性之研究
2-1 前言 34
2-2 實驗設備與實驗程序 35
2-2-1實驗設備 35
2-2-2實驗材料與實驗條件 44
2-2-3實驗步驟 46
2-3 實驗結果與討論 50
2-3-1 電弧放電圖 50
2-3-2 在界面之放電行為 55
2-3-3 銀接點表面的電蝕面積 62
2-3-4 靜態間隙的電弧相轉移 65
2-4 結論 67
第三章 靜態間隙銀接點損耗形態機制之研究
3-1 前言 69
3-2 實驗條件與程序 70
3-3 實驗結果與討論 73
3-3-1 電弧放電門檻圖 73
3-3-2 觀察陽極損耗的表面 76
3-3-3 電弧損耗的特性 85
3-3-4 極性對損耗形成的影響 92
3-4 結論 96
第四章 銀基接點材料的損耗與抗熔焊性能的分析
4-1 前言 98
4-2 實驗設備與實驗程序 100
4-2-1 實驗設備 100
4-2-2 實驗材料與實驗條件 105
4-2-3 實驗步驟 108
4-3 實驗結果與討論 109
4-3-1 材料的損耗與電弧的特性 109
4-3-2 接點表面的劣化分析 121
4-3-2-1 Ag-MeO接點表面的形態分析 121
4-3-2-2 X-ray繞射與熱分析 125
4-3-3 動態接點材料的熔焊特性 131
4-3-4 靜態間隙放電對接點材料的熔焊特性 138
4-4 結論 144
第五章 總結與展望
5-1 總結 146
5-2 展望 148
參考文獻 150
附錄A 161
附錄B 163
研究著作目錄 165
作者簡介 167

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