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完整後設資料紀錄
DC 欄位 | 值 | 語言 |
---|---|---|
dc.contributor.advisor | 林新智 | |
dc.contributor.author | Li-Jen Ho | en |
dc.contributor.author | 何立仁 | zh_TW |
dc.date.accessioned | 2021-06-08T03:32:23Z | - |
dc.date.copyright | 2019-08-16 | |
dc.date.issued | 2019 | |
dc.date.submitted | 2019-08-11 | |
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dc.identifier.uri | http://tdr.lib.ntu.edu.tw/jspui/handle/123456789/21375 | - |
dc.description.abstract | YOKE 8620MX鋼為商用合金鋼,在工業上的應用包括防墜器的吊鉤、海洋船隻鋼板等等。淬火後在常溫下最大抗拉強度可達1635MPa,經 600℃鹽浴回火後最大抗拉強度仍超過1000 MPa以上,屬於超高強度鋼。然而材料強度越高越容易受到氫脆的影響,發生氫脆便會造成工程上無法預測的破壞。本實驗透過電化學方式對YOKE 8620MX鋼進行充氫,利用常溫拉伸和低溫拉伸試驗,評估在不同的熱處理條件和不同拉伸溫度下,氫脆對材料機械性質之影響。並使用SEM、TEM來觀察不同熱處理條件下鋼材的微結構和拉伸破斷面,藉此釐清在不同狀況下對材料氫脆性質之影響。
實驗發現,YOKE 8620MX鋼在水淬態下,為板條狀麻田散鐵組織,擁有高差排密度,並觀察到少許自回火的板片。經200℃回火後,開始有細小ε碳化物在麻田散鐵板條之內析出,且差排密度下降,充氫後的吸氫量最低,使之有本研究次佳的抗氫脆能力。經400℃回火後,細小ε碳化物轉變為針狀的雪明碳鐵在麻田散鐵板片內析出,雪明碳鐵與回火麻田散鐵基地組織之介面為可逆氫捕集位置,使其充氫後的吸氫量高於回火200℃的吸氫量,抗氫脆能力因此下降。經600℃回火時,針狀的雪明碳鐵球化,且回火過程中內應力消除,使其差排密度最低,在本實驗中有最佳抗氫脆能力。 在不同溫度下拉伸,YOKE 8620MX鋼的延伸率隨溫度降低而降低,但延伸率損失率隨溫度下降並沒有顯著改變,由實驗可知低溫及充氫都使材料傾向發生脆性破壞,但兩者之間並沒有明顯之加成作用。YOKE 8620MX鋼只有在水淬態下,材料在達降伏強度之前就已經發生破壞,經回火後抗氫脆能力有顯著提升。 | zh_TW |
dc.description.abstract | YOKE 8620MX steel is a commercial alloy steel, and its industrial applications include hooks for fall arresters, marine steel plates, and so on. After quenching the ultimate tensile strength at room temperature can reach 1635Mpa, and the ultimate tensile strength after tempering in the salt bath at 600 °C is still more than 1000Mpa, which belongs to ultra-high strength steel. However, the higher the strength of the material, the more susceptible it is to hydrogen embrittlement , and the occurrence of hydrogen embrittlement can cause unpredictable damage to the project. In this experiment, YOKE 8620MX steel was charged hydrogen by electrochemical method. The effects of hydrogen embrittlement on the mechanical properties of the material under different heat treatment conditions and different tensile temperatures were evaluated by room temperature tensile tests and low temperature tensile tests. SEM and TEM were used to observe the microstructure and the fractured surface of the steel under different heat treatment conditions to clarifying the influence of the material on the hydrogen embrittlement properties under different conditions.
The experiment found that YOKE 8620MX steel in the water quenched state, is lath martensite structure, has the highest dislocation density, and observed a little self-tempered plate. After tempering at 200 °C, fine ε carbides began to precipitate in martensite, and the dislocation density was reduced. The hydrogen absorption after charging was the lowest, therefore it has the better resistance to hydrogen embrittlement. After tempering at 400 °C, fine ε carbides are transformed into cementite precipitated in temper martensite matrix. The interface between cementite and the temper martensite matrix is a reversible hydrogen trapping site, which makes the hydrogen absorption capacity is higher than 200 ° C, and the hydrogen embrittlement resistance is thus lowered. When tempered at 600 ° C, cementite is spheroidized. At this time, due to the elimination of internal stress during the tempering process, dislocation density is the smallest, and the best hydrogen embrittlement resistance ability is obtained in this experiment. When doing tensile test at different temperatures, the elongation of YOKE 8620MX steel decreases with decreasing temperature, but the elongation loss rate does not change significantly with temperature. It is known from experiments that both low temperature and hydrogen charging tend to cause brittle failure, but there is no obvious additive effect between them. YOKE 8620MX steel only in the water quenched state, the material has been destroyed before the yield strength, after tempering, the ability to resist hydrogen embrittlement has been improved. | en |
dc.description.provenance | Made available in DSpace on 2021-06-08T03:32:23Z (GMT). No. of bitstreams: 1 ntu-108-R06527056-1.pdf: 9828501 bytes, checksum: a94abc5d16352660622db9459b9497bb (MD5) Previous issue date: 2019 | en |
dc.description.tableofcontents | 誌謝 I
摘要 II Abstract III 目錄 V 圖目錄 VII 表目錄 X 第一章 前言 1 第二章 文獻回顧 2 2.1 YOKE 8620MX簡介 2 2.2 合金添加 2 2.2.1 碳 2 2.2.2 硼 2 2.2.3 鉬 3 2.2.4 鈦 3 2.2.5 鉻 3 2.2.6 錳 4 2.2.7 矽 4 2.2.8 鎳 4 2.2.9 磷 4 2.2.10 硫 4 2.3 鋼鐵組織介紹 5 2.3.1 麻田散鐵 5 2.3.2 麻田散鐵轉變溫度 6 2.3.3 碳含量對麻田散鐵的影響 8 2.3.4 回火麻田散鐵與碳化物 10 2.3.5 殘留沃斯田鐵 13 2.3.6 自回火麻田散鐵 14 2.4 氫脆簡介 15 2.5 氫如何進入材料內部 15 2.6 氫捕集位置 (Hydrogen Trapping Site) 17 2.7 元素添加對氫脆的影響 19 2.8 氫在材料內的擴散 19 2.9 氫脆理論 20 2.9.1 氫化物形成理論 (Hydride Formation) 20 2.9.2 氫致弱化建結理論 (Hydrogen Enhanced Decohesion, HEDE) 21 2.9.3 氫致局部塑性變形理論 (Hydrogen Enhanced Local Plasticity, HELP) 23 2.9.4 差排發射理論(Adsorption-induced dislocation emission, AIDE) 26 2.9.5 綜合機制 (Hybrid mechanisms) 28 2.10 熱脫氫 (thermal desorption spectroscopy, TDS) 29 2.11 破斷形貌 31 2.11.1 渦穴組織 32 2.11.2 劈裂組織 32 2.11.3 半劈裂組織 33 2.11.4 沿晶破壞 33 2.11.5 混合型破斷 34 第三章 實驗方法 35 3.1 實驗流程 35 3.2 合金成分設計 35 3.3 合金成分分析 36 3.4 熱膨脹儀分析 36 3.5 鋼材熱處理 36 3.6 試片加工 37 3.7 金相觀察實驗 38 3.8 TEM觀察實驗 39 3.9 電化學充氫 39 3.10 拉伸試驗 40 3.11 熱脫氫分析 40 3.12 喬米尼試驗與硬化能 41 3.13 硬度試驗 41 3.14 衝擊試驗 41 第四章 結果與討論 42 4.1 成分分析 42 4.2 熱膨脹儀分析 42 4.3 喬米尼分析 43 4.4 原沃斯田鐵組織觀察 43 4.5 淬火與回火組織觀察 44 4.6 麻田散鐵顯微組織之TEM觀察 46 4.6.1 淬火態之麻田散鐵組織觀察 46 4.6.2 回火200℃之麻田散鐵組織觀察 46 4.6.3 回火400℃之麻田散鐵組織觀察 47 4.6.4 回火600℃之麻田散鐵組織觀察 48 4.7 硬度試驗 50 4.8 衝擊試驗 50 4.9 差排密度觀察與量測 51 4.10 熱脫氫試驗 53 4.10.1 氫含量分析 53 4.10.2 氫捕集位置之活化能分析 54 4.11 拉伸試驗 57 4.11.1 低溫拉伸試驗 57 4.11.2 充氫拉伸試驗 61 4.11.3 低溫與充氫對材料的影響 67 4.12 破斷面觀察 68 4.12.1 常溫及低溫破斷面 68 4.12.2 充氫破斷面 74 第五章 結論 81 第六章 參考文獻 82 圖目錄 圖2- 1 鐵碳平衡圖[2] 5 圖2- 2 沃斯田鐵轉變麻田散鐵示意圖[10] 6 圖2- 3 不同尺度麻田散鐵示意圖[11] 6 圖2- 4 連續冷卻曲線[2] 7 圖2- 5 合金元素與Ms溫度關係圖[12] 7 圖2- 6板條狀麻田散鐵與板片狀麻田散鐵[13] 8 圖2- 7 碳含量、回火溫度與麻田散鐵硬度關係圖[14] 9 圖2- 8 碳含量與麻田散鐵轉變溫度關係圖[12] 9 圖2- 9 板條內雪明碳鐵形貌[18] 11 圖2- 10 板條間雪明碳鐵影像:(a)明場影像(b)暗場影像[20] 12 圖2- 11 球化雪明碳鐵(700℃回火)[18] 12 圖2- 12 麻田散鐵回復(左)與再結晶(右)[21] 13 圖2- 13殘留沃斯田鐵形貌:(上)明場影像(下)暗場影像[22] 14 圖2- 14自回火麻田散鐵影像[21] 14 圖2- 15 氫氣分子進入材料內部流程圖[26] 16 圖2- 16 氫氣分子透過溢出機制進入材料流程圖[26] 16 圖2- 17 材料內部的氫捕集位置[31] 18 圖2- 18 不同捕集位置對氫移動的影響[34] 18 圖2- 19氫在不同材料中的擴散系數[31] 20 圖2- 20 氫化物氫脆理論示意圖[31] 21 圖2- 21 HEDE氫脆理論示意圖[31] 22 圖2- 22 不同氫分壓下的裂縫角度,氫氣壓由左自右分別為10Pa、0.7Pa、真空中[52] 23 圖2- 23 不同氫分壓與裂縫角度關係[52] 23 圖2- 24 HELP氫脆理論示意圖[31] 24 圖2- 25氫對差排移動性的影響[58] 25 圖2- 26 氫對差排間距的影響[58] 25 圖2- 27 微孔洞聚集斷裂 (MVC)示意圖[31] 27 圖2- 28 窩穴破斷形成機制示意圖[66] 27 圖2- 29 AIDE氫脆理論示意圖[31] 28 圖2- 30差排發射理論綜合氫致局部塑性變形理論和氫致弱化鍵結理論[31] 29 圖2- 31差排發射理論綜合氫致弱化鍵結理論[31] 29 圖2- 32 Ferrite-Banite steel和TRIP steel在不同升溫速率下的TDS曲線[73] 31 圖2- 33 窩穴組織[66] 32 圖2- 34 典型劈裂破壞之河道紋[66] 33 圖2- 35 鋸齒狀的半劈裂破斷形貌[55] 33 圖2- 36 沿晶破斷形貌[78] 34 圖2- 37 氫致混和型破斷面[79] 34 圖3- 1 實驗流程圖 35 圖3- 2 熱處理示意圖 37 圖3- 3 拉伸試棒尺寸規格 37 圖3- 4 衝擊試棒尺寸規格,單位mm 38 圖3- 5 熱脫氫分析試片尺寸規格,單位mm 38 圖3- 6 喬米尼試驗試棒尺寸規格,單位mm 38 圖3- 7 電化學充氫實驗裝置圖 39 圖3- 8 熱脫氫設備 40 圖4- 1 熱膨脹儀分析結果 42 圖4- 2 喬米尼硬化能曲線 43 圖4- 3 YOKE 8620MX 原沃斯田鐵組織 43 圖4- 4 YOKE 8620MX鋼顯微組織 44 圖4- 5 YOKE 8620MX鋼回火400℃顯微組織 45 圖4- 6 YOKE 8620MX鋼回火600℃顯微組織 45 圖4- 7 YOKE 8620MX鋼於水淬態之顯微組織: 46 圖4- 8 YOKE 8620MX鋼於200℃回火後之顯微組織: 47 圖4- 9 YOKE 8620MX鋼於400℃回火後之顯微組織: 48 圖4- 10 YOKE 8620MX鋼於600℃回火後之顯微組織: 49 圖4- 11淬火態及不同回火溫度之衝擊韌性 50 圖4- 12回火400℃之韌脆轉換 51 圖4- 13 YOKE 8620MX鋼在不同熱處理狀態下之差排形貌:(a)水淬態 (b)200℃回火 (c) 400℃回火 (d) 600℃回火 52 圖4- 14 YOKE 8620MX鋼在不同熱處理狀態下之差排密度 52 圖4- 15 YOKE 8620MX鋼在不同熱處理狀態下之氫含量 53 圖4- 16水淬態下常溫脫氫4小時後不同升溫速率之TDS曲線 55 圖4- 17回火200℃下常溫脫氫4小時後不同升溫速率之TDS曲線 55 圖4- 18回火400℃下常溫脫氫4小時後不同升溫速率之TDS曲線 56 圖4- 19回火600℃下常溫脫氫4小時後不同升溫速率之TDS曲線 56 圖4- 20水淬態於常溫及低溫之拉伸曲線 58 圖4- 21 200℃回火態,常溫及低溫之拉伸曲線 59 圖4- 22 400℃回火態下,常溫及低溫之拉伸曲線 59 圖4- 23 600℃回火態下,常溫及低溫之拉伸曲線 60 圖4- 24 YOKE 8620MX鋼未充氫拉伸之最大抗拉強度(UTS)比較 60 圖4- 25 YOKE 8620MX鋼未充氫拉伸之延伸率(%)比較 61 圖4- 26水淬態充氫後於常溫及低溫之拉伸曲線 62 圖4- 27 200℃回火態充氫後,常溫及低溫之拉伸曲線 63 圖4- 28 400℃回火態充氫後,常溫及低溫之拉伸曲線 63 圖4- 29 600℃回火態充氫後,常溫及低溫之拉伸曲線 64 圖4- 30 YOKE 8620MX鋼充氫拉伸後最大抗拉強度(UTS)比較 64 圖4- 31 YOKE 8620MX鋼充氫拉伸後延伸率(%)比較 65 圖4- 32 YOKE 8620MX鋼在不同狀態下充氫與未充氫UTS比較 65 圖4- 33 YOKE 8620MX鋼在不同狀態下充氫與未充氫延伸率比較 66 圖4- 34 YOKE 8620MX鋼在不同狀態下的延伸損失率 66 圖4- 35回火200℃,常溫、低溫、低溫充氫拉伸比較 67 圖4- 36 YOKE 8620MX淬火態未充氫常溫拉伸破斷面: 68 圖4- 37 YOKE 8620MX淬火態未充氫-40℃拉伸破斷面: 69 圖4- 38 YOKE 8620MX淬火態未充氫-60℃拉伸破斷面: 69 圖4- 39 YOKE 8620MX回火200℃未充氫常溫拉伸破斷面: 70 圖4- 40 YOKE 8620MX回火200℃未充氫-40℃拉伸破斷面: 70 圖4- 41 YOKE 8620MX回火200℃未充氫-60℃拉伸破斷面: 71 圖4- 42 YOKE 8620MX回火400℃未充氫常溫拉伸破斷面: 71 圖4- 43 YOKE 8620MX回火400℃未充氫-40℃拉伸破斷面: 72 圖4- 44 YOKE 8620MX回火400℃未充氫-60℃拉伸破斷面: 72 圖4- 45 YOKE 8620MX回火600℃未充氫常溫拉伸破斷面: 73 圖4- 46 YOKE 8620MX回火600℃未充氫-40℃拉伸破斷面: 73 圖4- 47 YOKE 8620MX回火600℃未充氫-60℃拉伸破斷面: 74 圖4- 48 YOKE 8620MX淬火態充氫常溫拉伸破斷面: 75 圖4- 49 YOKE 8620MX淬火態充氫-40℃拉伸破斷面: 75 圖4- 50 YOKE 8620MX淬火態充氫-60℃拉伸破斷面: 76 圖4- 51 YOKE 8620MX回火200℃充氫常溫拉伸破斷面: 76 圖4- 52 YOKE 8620MX回火200℃充氫-40℃拉伸破斷面: 77 圖4- 53 YOKE 8620MX回火200℃充氫-60℃拉伸破斷面: 77 圖4- 54 YOKE 8620MX回火400℃充氫常溫拉伸破斷面: 78 圖4- 55 YOKE 8620MX回火400℃充氫-40℃拉伸破斷面: 78 圖4- 56 YOKE 8620MX回火400℃充氫-60℃拉伸破斷面: 79 圖4- 57 YOKE 8620MX回火600℃常溫充氫拉伸破斷面: 79 圖4- 58 YOKE 8620MX回火600℃充氫-40℃拉伸破斷面: 80 圖4- 59 YOKE 8620MX回火600℃充氫-60℃拉伸破斷面: 80 表目錄 表2- 1 不同捕集位置之活化能[1] 31 表3- 1 YOKE 8620MX 合金成分設計含量,單位wt.% 36 表4- 1 分光成分,單位wt.% 42 表4- 2 TDS結果整理 57 | |
dc.language.iso | zh-TW | |
dc.title | 熱處理對 YOKE 8620MX鋼氫脆性質影響之研究 | zh_TW |
dc.title | The influence of heat treatment on the hydrogen embrittlement of YOKE 8620MX steel | en |
dc.type | Thesis | |
dc.date.schoolyear | 107-2 | |
dc.description.degree | 碩士 | |
dc.contributor.oralexamcommittee | 吳錫侃,楊哲人,陳志遠 | |
dc.subject.keyword | YOKE 8620MX鋼,麻田散鐵,氫脆,低溫拉伸,回火處理, | zh_TW |
dc.subject.keyword | YOKE 8620MX steel,martensit,hydrogen embrittlement,low temperature tensile test,tempering, | en |
dc.relation.page | 90 | |
dc.identifier.doi | 10.6342/NTU201902891 | |
dc.rights.note | 未授權 | |
dc.date.accepted | 2019-08-12 | |
dc.contributor.author-college | 工學院 | zh_TW |
dc.contributor.author-dept | 材料科學與工程學研究所 | zh_TW |
顯示於系所單位: | 材料科學與工程學系 |
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