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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 | Wen-Hao Chien | en |
dc.contributor.author | 簡文昊 | zh_TW |
dc.date.accessioned | 2021-07-10T21:36:15Z | - |
dc.date.available | 2021-07-10T21:36:15Z | - |
dc.date.copyright | 2016-10-14 | |
dc.date.issued | 2016 | |
dc.date.submitted | 2016-07-21 | |
dc.identifier.citation | 參考文獻
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dc.identifier.uri | http://tdr.lib.ntu.edu.tw/jspui/handle/123456789/76752 | - |
dc.description.abstract | 15B30為硼系超高強度鋼,在結構鋼及汽車鋼板應用上有出色的表現。淬火後呈現麻田散鐵組織,其抗拉強度高達1768Mpa,再經由200℃~400℃回火後顯現回火麻田散鐵組織,其抗拉強度仍可維持1200MPa以上。然而超高強度鋼之缺點為易受到氫脆效應的影響,在應用上此因素可能會造成無法預測之破壞。本實驗研究之目的為利用化學充氫及拉伸試驗檢測15B30鋼材之氫脆以及延遲破壞行為,並實施深冷處理與不同回火熱處理程序,藉以改善15B30鋼材之氫脆現象。
未實施深冷處理時,15b30水淬後仍有約3.6%的殘留沃斯田鐵組織,殘留沃斯田鐵組織存在於原沃斯田鐵晶界以及麻田散鐵板條間。15b30其淬火態之抗氫脆能力差,回火過後抗氫脆能力有明顯的提升,其中200℃回火時,其抗氫脆能力最佳,主要之原因為在低溫回火時,麻田散鐵板條內部析出細小的碳化物,提供了氫捕集位置,但在300℃以及400℃回火時,殘留沃斯田鐵會分解並析出碳化物。而此類碳化物屬於非整合性(incoherent)析出物,為不可逆之氫捕集位置,其周圍會有較多量之氫原子聚集,因而容易誘發氫脆現象。 15B30合金鋼淬火組織經過深冷處理後,其抗氫脆能力可明顯提升。此現象係因為深冷處理可以降低存在於麻田散鐵板條介面之殘留沃斯田鐵量,因而可減少300℃及400℃回火時於板條介面產生粗大碳化物,進而有效提升其抗氫脆能力。 | zh_TW |
dc.description.abstract | 15B30 steel is an ultra-high strength boron steel and exhibits excellent performance in the structural and automotive applications. It exhibits a high tensile strength of 1768MPa in the as-quenched state. After tempering at 200℃~400℃, its tensile strength still remains above 1200Mpa. However, the ultra-high strength steels are prone to suffer the problem of hydrogen embrittlement, which will induce the unpredicted fracture during the practical applications. The present study aims at examining the behavior of hydrogen embrittlement of the 15B30 steel, by using the methods of hydrogen charging and mechanical tensile test. Meanwhile, the sub-zero treatment and a series of tempering processes are also carried out to improve the hydrogen embrittlement of 15B30 steel.
The as-quenched 15B30 specimen without sub-zero treatment has about 3.6% retained austenite which exists along the prior austenite grain boundaries and the interfaces between martensite laths. The as-quenched 15B30 exhibits a worse resistance of hydrogen embrittlement. After tempering, the resistance of hydrogen embrittlement is improved significantly. The specimen with 200℃ tempering has the best resistance of hydrogen embrittlement. This feature is ascribed to the formation of fine carbides within the interior of martensite laths. These fine carbides can provide the hydrogen-trapping sites. However, during the tempering at 300℃ and 400℃, the retained austenite will decompose and the cementite forms. The cementite precipitated at higher temperatures is incoherent and belongs to the irreversible hydrogen trapping site. More hydrogen atoms will concentrate around these sites and result in a weak resistance of hydrogen embrittlement. The as-quenched 15B30 specimen can increase obviously the resistance of hydrogen embrittlement through the sub-zero treatment. This feature is ascribed to that the sub-zero treatment reduces the amount of retained austenite and leads to the reduction of coarse cementite precipitated at the interfaces between martensite laths during the tempering process. Therefore, the resistance of hydrogen embrittlement of 15B30 steels can be effectively improved even after tempering at 300℃ and 400℃. | en |
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dc.description.tableofcontents | 目錄
誌謝 II 摘要 III Abstract IV 目錄 VI 圖目錄 IX 表目錄 XII 第一章 前言 1 第二章 文獻回顧 2 2-1鋼鐵簡介 2 2-2熱處理簡介 2 2-2-1退火(Anneling) 3 2-2-2正常化 3 2-2-3淬火 4 2-2-4深冷 4 2-2-5回火 4 2-3組織簡介 5 2-3-1麻田散鐵與回火麻田散鐵 5 2-3-2殘留沃斯田鐵 10 2-4合金元素簡介 12 2-4-1 硼(Boron) 12 2-4-2 矽(Silicon) 12 2-4-3 錳(Manganese) 12 2-4-4 鉻(Chromium) 13 2-4-5 鈦(Titanium) 13 2-5先進高強度鋼(AHSS)簡介 13 2-6 氫對材料之影響 14 2-6-1 氫的來源 14 2-6-2 氫如何進入材料內部 14 2-6-3 材料內部之氫捕集位置 15 2-6-4 氫在材料內部之滲透性(Permeability)、擴散速率(Diffusivity)及溶解度(Solubility) 18 2-7 氫致破壞 23 2-7-1 氫誘發氣泡 23 2-7-2 氫氣析出造成破壞 24 2-7-3 氫攻擊 25 2-8 氫脆理論 25 2-8-1 氫致弱化鍵結理論(Hydrogen enhanced decohesion, HEDE) 26 2-8-2 差排發射理論(Adsorption Induced Dislocation Emission, AIDE) 29 2-8-3 氫致局部塑性變形理論(Hydrogen Enhanced Localized Plasticity, HELP) 31 2-8-4 綜合機制(Hybrid mechanisms) 31 2-9 延遲破壞 34 2-10 影響氫脆的參數 36 2-10-1 氫濃度對氫脆之影響 36 2-10-2 應變速率對氫脆之影響 38 2-10-3 溫度對氫脆之影響 39 2-11 鋼鐵組織與氫脆關係 40 2-11-1 殘留沃斯田鐵對氫脆之影響 40 2-11-2 麻田散鐵與回火麻田散鐵對氫脆之影響 41 2-11-3 原沃斯田鐵晶界對氫脆之影響 42 2-12 超高強度合金鋼與氫脆關係 43 2-13 氫脆效應所導致的破斷形貌 45 第三章 實驗步驟 47 3-1 實驗流程 47 3-2 15B30鋼材 47 3-3 試片加工與熱處理 48 3-4 硬度測驗 49 3-5 顯微組織觀察 50 3-6 陰極化學充氫 50 3-7 拉伸試驗以及定應力試驗 51 第四章 結果與討論 53 4-1 成分分析 53 4-2 硬度分析 53 4-3 原沃斯田鐵組織鑑定 54 4-4 淬火與回火組織鑑定 55 4-5 深冷處理前後之殘留沃斯田鐵(Retained austenite, R.A.)觀察 56 4-6 深冷處理前後之殘留沃斯田鐵含量鑑定 56 4-7 回火麻田散鐵之TEM觀察 57 4-7-1 回火麻田散鐵板條內碳化物析出觀察 57 4-7-2 回火麻田散鐵碳化物析出位置觀察 59 4-7-3 深冷處理與否對碳化物析出形貌之觀察 60 4-8 拉伸試驗 62 4-8-1 空氣中的拉伸 62 4-8-2 充氫拉伸實驗 63 4-8-3 定應力拉伸實驗 69 4-9 破斷面觀察 70 4-9-1 空氣中拉伸之破斷面 70 4-9-2 充氫拉伸之破斷面 73 4-9-3 定應力拉伸之破斷面 79 第五章 結論 84 第六章 參考文獻 85 圖目錄 圖2-1 鐵碳平衡圖[1] 5 圖2-2 沃斯田鐵轉變為麻田散鐵結構示意圖[2] 6 圖2-3 板條內雪明碳鐵形貌:(A)明場影像;(B)暗場影像。[6] 8 圖2-4 板條介面雪明碳鐵形貌:(A)明場影像;(B)暗場影像;(C)繞射圖。[6] 9 圖2-5 合金元素含量所對應之殘留沃斯田鐵含量關係。 11 圖2-6 FE-1CR-2MO-0.3C鋼材870℃水淬後殘留沃斯田鐵形貌: 11 圖2-7 先進高強度鋼之強度延性分佈。 13 圖2-8氣相氫分子(H2)進入材料內部過程。[23] 15 圖2-9 材料內部之氫捕集位置: 17 圖2-10不同種類氫捕集位置對於氫脆所產生的影響: 17 圖2-11電化學氫滲透測試示意圖。 20 圖2-12 FE_0.45WT%C_1.5WT%MO在20℃時不同氫濃度與有效擴散係數之關係。 20 圖2-13 FE_0.45WT%C_1.5WT%MO在不同溫度下所量測到之有效擴散係數。 21 圖2-14 不同種類鋼材在不同溫度下之滲透率。 21 圖2-15 不同種類鋼材在不同溫度下之擴散率。 22 圖2-16 氫在經過退火狀態下純鐵中之擴散係數。 23 圖2-17 氫誘發腫泡及內部氫氣析出造成破壞 24 圖2-18 氫脆因素 26 圖2-19 HEDE 氫脆理論示意圖 27 圖2-20 FE-3WT%SI單晶中,裂縫尖端之角度 28 圖2-21 不同的氫氣分壓與裂縫尖端角度之關係 28 圖2-22 微孔洞聚集斷裂(MVC)示意圖 30 圖2-23 AIDE破斷機制示意圖 30 圖2-24 HELP之破斷理論示意 31 圖2-25 AIDE主導的破斷機制與HELP以及HEDE交互作用 33 圖2-26 AIDE與HEDE交互作用 33 圖2-27延遲破壞之施加應力與破斷時間關係: 35 圖2-28 在氫環境下應力集中因子對裂縫成長速度的影響。 35 圖2-29各種高強度合金之擴散係數與II階段裂縫成長速率之關係 36 圖2-30 IN903之氫濃度與應力集中因子關係 37 圖2-31 18NI鋼之環境氫壓力與裂縫成長速率關係 37 圖2-32 充氫後的破斷強度(FC)及材料本身強度(F0)之比值與應變速率的關係 38 圖2-33 IN903在充氫的條件下裂縫成長速率及應力集中因子對不同溫度的關係。 39 圖2-34 殘留沃斯田鐵與基材介面特性: 41 圖2-35 晶粒大小與應力集中因子關係。 43 圖2-36 材料局部降伏強度以及鍵結力與氫含量關係。 44 圖2-37 材料發生氫脆破壞過程中之氫的來源、移動方式、可能存在位置,其對應所造成的破壞形貌 46 圖3-1 實驗流程圖 47 圖3-2 本研究15B30鋼材之熱處理流程 49 圖3-3 洛氏硬度計 49 圖3-4 本實驗所使用之化學充氫設備 51 圖3-5 15B30拉伸試片規格 52 圖4-1 不同熱處理參數鋼材之硬度值 54 圖4-2 15B30鋼材之原沃斯田鐵組織 54 圖4-3 15B30鋼材淬火與回火組織鑑定: 55 圖4-4 深冷處理前後之殘留沃斯田鐵觀察: 56 圖4-5 15B30殘留沃斯田鐵含量EBSD掃描結果: 57 圖4-6 15B30鋼材200OC回火,板條內部析出之碳化物觀察: 58 圖4-7 15B30鋼材300OC回火,板條內部析出之碳化物觀察: 58 圖4-8 15B30鋼材400OC回火,板條內部析出之碳化物觀察: 59 圖4-9 15B30鋼材在不同回火溫度,碳化物分佈位置的觀察: 60 圖4-10 15B30鋼材在回火溫度為300OC時,碳化物析出形貌觀察: 61 圖4-11 15B30鋼材在回火溫度為400OC時,碳化物析出形貌觀察: 61 圖4-12 深冷處理與否15B30鋼材之最大抗拉強度比較 62 圖4-13 15B30鋼材水淬狀態之充氫拉伸結果 64 圖4-14 15B30鋼材回火200OC狀態之充氫拉伸結果 64 圖4-15 15B30鋼材回火300OC狀態之充氫拉伸結果 65 圖4-16 15B30鋼材回火400OC狀態之充氫拉伸結果 65 圖4-17 15B30鋼材水淬+深冷處理狀態之充氫拉伸結果 66 圖4-18 15B30鋼材水淬+深冷處理回火200OC狀態之充氫拉伸結果 66 圖4-19 15B30鋼材水淬+深冷處理回火300OC狀態之充氫拉伸結果 67 圖4-20 15B30鋼材水淬+深冷處理回火400OC狀態之充氫拉伸結果 67 圖4-21 不同熱處理程序15B30鋼材之充氫拉伸結果 68 圖4-22 15B30鋼材各回火參數對應其定應力存活時間 70 圖4-23 15B30淬火態未充氫拉伸破斷面: 71 圖4-24 15B30回火200OC未充氫拉伸破斷面: 71 圖4-25 15B30回火300OC未充氫拉伸破斷面: 72 圖4-26 15B30回火400OC未充氫拉伸破斷面: 72 圖4-27 15B30淬火態充氫拉伸破斷面: 74 圖4-28 15B30回火200OC充氫拉伸破斷面: 74 圖4-29 15B30回火300OC充氫拉伸破斷面: 75 圖4-30 15B30回火400OC充氫拉伸破斷面: 75 圖4-31 15B30淬火+深冷充氫拉伸破斷面: 77 圖4-32 15B30深冷後回火200OC充氫拉伸試片破斷面: 77 圖4-33 15B30深冷後回火300OC充氫拉伸試片破斷面: 78 圖4-34 15B30深冷後回火400OC充氫拉伸試片破斷面: 78 圖4-35 15B30淬火態充氫定應力拉伸破斷面: 79 圖4-36 15B30回火200OC充氫定應力拉伸破斷面: 80 圖4-37 15B30回火300OC充氫定應力拉伸破斷面: 80 圖4-38 15B30回火400OC充氫定應力拉伸破斷面: 81 圖 4-39 15B30淬火+深冷充氫定應力拉伸破斷面: 82 圖4-40 15B30深冷後回火200OC充氫定應力拉伸試片破斷面: 82 圖4-41 15B30深冷後回火300OC充氫定應力拉伸試片破斷面: 83 圖4-42 15B30深冷後回火400OC充氫定應力拉伸試片破斷面: 83 表目錄 表2-1 不同種類補集位置之熱脫附溫度以及活化能 18 表3-1 15B30各成份設計含量 48 表3-2 本實驗拉伸試片所採用之規範 52 表3-3瓦茲浴法鍍鎳溶液成分。 52 表4-1 15B30各成份設計含量 53 表4-2 15B30各成份實際檢測含量 53 表4-3 15B30鋼材各回火參數之最大抗拉強度(MPA) 62 表4-4定應力拉伸實驗之設定應力參數(MPA) 69 表4-5 15B30鋼材各回火參數之定應力存活時間(SEC.) 69 | |
dc.language.iso | zh-TW | |
dc.title | 深冷處理與熱處理程序對硼系超高強度鋼之
氫脆性質研究 | zh_TW |
dc.title | The influence of sub-zero and tempering treatments on the hydrogen embrittlement of ultra-high strength boron steel | en |
dc.type | Thesis | |
dc.date.schoolyear | 104-2 | |
dc.description.degree | 碩士 | |
dc.contributor.oralexamcommittee | 楊哲人,薛人愷,蔡履文,黃慶淵 | |
dc.subject.keyword | 超高強度鋼,深冷處理,回火麻田散鐵,氫脆, | zh_TW |
dc.subject.keyword | ultra-high strength steel,sub-zero treatment,tempered martensite,hydrogen embrittlement, | en |
dc.relation.page | 92 | |
dc.identifier.doi | 10.6342/NTU201601193 | |
dc.rights.note | 未授權 | |
dc.date.accepted | 2016-07-22 | |
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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