請用此 Handle URI 來引用此文件:
http://tdr.lib.ntu.edu.tw/jspui/handle/123456789/64564
完整後設資料紀錄
DC 欄位 | 值 | 語言 |
---|---|---|
dc.contributor.advisor | 薛人愷(Ren-Kai Shiue) | |
dc.contributor.author | Yueh-Hsuan Tsai | en |
dc.contributor.author | 蔡岳軒 | zh_TW |
dc.date.accessioned | 2021-06-16T17:54:50Z | - |
dc.date.available | 2015-08-19 | |
dc.date.copyright | 2012-08-19 | |
dc.date.issued | 2012 | |
dc.date.submitted | 2012-08-13 | |
dc.identifier.citation | [1] T. Angel, 'Formation of Martensite in Austenitic Stainless Steels - Effects of Deformation, Temperature, and Composition,' Journal of the Iron and Steel Institute, vol. 177, pp. 165-&, 1954.
[2] 'Assessment and Management of Aging of Major Nuclear Power Plant Components Important to Safety,' International Atomic Energy Agency2003. [3] N. Taylor, et al., 'Assessment of Dissimilar Weld Integrity: Final Report of the NESC-III Project,' Directorate-General Joint Research Centre Institute for Energy, Petten (the Netherlands)2006. [4] E. E. Lewis, Fundamentals of Nuclear Reactor Physics: Academic Press, 2008. [5] G. T. Miller, Living in the Environment: Principles, Connections, and Solutions, 13th ed.: Brooks Cole, 2003. [6] 劉衛蒼, '世界各先進國家核子反應爐簡介,' Army Bimonthly, vol. 519, pp. 144-152, 2011. [7] 馬進, et al., 核能發電原理: 中國電力出版社, 2007. [8] 李敏, '核分裂反應器的發展歷程,' 科學月刊 Science monthly, vol. 494, pp. 118-132, 2011. [9] S. Glasstone and A. Sesonske, Nuclear Reactor Engineering: Reactor Design Basics, 4th ed.: Springer, 1994. [10] 中華民國核能學會. (03/01). 核能百科. Available: http://www.chns.org/s.php?id=47&id2=210 [11] 郭榮卿, '核電廠材料劣化與對策研究:現況與規劃,' presented at the 2006台灣原子能論壇, 2006. [12] H.-C. Lee, 'Development of Nuclear Pressure Vessel Materials,' presented at the 17th Summer Seminar on Fusion Reactor Technology, Seoul, Korea, 2001. [13] A. Dhooge, et al., 'A Review of Work Related to Reheat Cracking in Nuclear Reactor Pressure Vessel Steels,' International Journal of Pressure Vessels and Piping, vol. 6, pp. 329 - 409, 1978. [14] B. D. Cullity and S. R. Stock, Eds., Elements of X-Ray Diffraction. Upper Saddle River, New Jersey 07458: Prentice-Hall, Inc., 2001, p.^pp. Pages. [15] J. W. Christian, Martensite—Fundamentals and Technology. London: Longman, 1970. [16] G. Krauss, Steels: Heat Treatment and Processing Principles, 1990. [17] W. A. J. Albert, 'Uber Treibseile am Harz,' Archive fur Mineralogie, Geognosie, Bergbau und Huttenkunde, vol. 10, pp. 215-234, 1838. [18] F. Braithwaite., 'On the Fatigue and Consequent Fracture of Metals,' Institution of Civil Engineers, Minutes of Proceedings, pp. 463-474, 1854. [19] A. Wohler, 'Theorie Rechtekiger Eiserner Bruckenbalken mit Gitterwanden und mit Blechwanden,' Zeitschrift fur Bauwesen, vol. 5, pp. 121-166, 1855. [20] L. F. Coffin, 'A Study of the Effects of Cyclic Thermal Stresses on A Ductile Metal,' Trans. ASME J. appl. Mech., vol. 74, pp. 931–950, 1954. [21] P. C. Paris, et al., 'A Rational Analytic Theory of Fatigue,' The Trend in Engineering, vol. 13, p. 9, 1961. [22] J. A. Ewing and J. C. W. Humfrey, 'The fracture of metals under repeated alternations of stress,' Phil. Trans. R. Society, London, vol. CC, pp. 241 - 250, 1903. [23] A. A. Griffith, 'The Phenomenon of Rupture and Flow in Solids,' Philosophical Transactions of the Royal Society A, vol. A221, p. 163, 1920. [24] S. V. Serensen, 'The Endurance of Metals and the Design of Machine Components,' M. L. Gos Izd-vo Teckhnich Liter., 1937. [25] M. A. Miner, 'Cumulative Damage in Fatigue,' Trans. ASME J. appl. Mech., vol. 12, pp. A159 - A164, 1945. [26] S. V. Serensen, 'Theory of Strength Under Variable Loading,' Akademici Nauk Ukrainskoc, SSR. Nukwoi pratsi Instytuta Budivel noi K. McKhani, 1940. [27] G. R. Irwin, 'Fracture Dynamics: Fracturing of Metals,' American Society for Metals, pp. 147 - 166, 1948. [28] R. O. Ritchie, 'Near-threshold Fatigue-crack Propagation in Steels,' International Metals Reviews, vol. 24, pp. 205-230, 1979. [29] J. Lankford and F. N. Kusenberger, 'On Crack Tip Yielding During Fatigue Cycling of A High-strength Steel,' Philosophical Magazine, vol. 26, pp. 1485-1490, 1972/12/01 1972. [30] J. H. Huang and C. J. Altstetter, 'Internal Hydrogen-induced Subcritical Crack-growth in Austenitic Stainless-steels,' Metallurgical Transactions a-Physical Metallurgy and Materials Science, vol. 22, pp. 2605-2618, Nov 1991. [31] A. G. Pineau and R. M. Pelloux, 'Influence of Strain-induced Martensitic Transformations on Fatigue Crack Growth-rates in Stainless-steels,' Metallurgical Transactions, vol. 5, pp. 1103-1112, 1974. [32] K. Rajanna, et al., 'X-ray Fractography Studies on Austenitic Stainless Steels,' Engineering Fracture Mechanics, vol. 54, pp. 155-&, May 1996. [33] G. Schuster and C. Altstetter, 'Fatigue of Annealed and Cold-worked Stable and Unstable Stainless-steels,' Metallurgical Transactions a-Physical Metallurgy and Materials Science, vol. 14, pp. 2077-2084, 1983. [34] S. Singh and C. Altstetter, 'Effects of Hydrogen Concentration on Slow Crack Growth in Stainless Steels,' Metall. Trans. A, vol. 13A, pp. 1799 - 1808, 1982. [35] S. G. and A. C., Metallurgical Transactions A, vol. 14, pp. 2077-2084., 1983. [36] N. Narita and H. K. Birnbaum, 'On the Role of Phase-transitions in the Hydrogen Embrittlement of Stainless-steels,' Scripta Metallurgica, vol. 14, pp. 1355-1358, 1980. [37] S. Suresh and R. O. Ritchie, 'Propagation of Short Fatigue Cracks,' International Metals Reviews, vol. 29, pp. 445-475, 1984. [38] C. A. Zapffe and C. E. Sims, 'Hydrogen Embrittlement, Internal Stress and Defects in Steel,' Transactions of the American Institute of Mining and Metallurgical Engineers, vol. 145, pp. 225-261, 1941. [39] N. J. Petch and P. Stables, 'Delayed Fracture of Metals Under Static Load,' Nature, vol. 169, pp. 842-843, 1952. [40] H. H. Johnson, et al., 'Hydrogen, Crack Initiation, and Delayed Failure in Steel,' Journal Name: Trans. Met. Soc. AIME; Journal Volume: Vol: 212; Other Information: Orig. Receipt Date: 31-DEC-58, pp. Medium: X; Size: Pages: 528-36, 1958. [41] C. D. Beachem, 'New Model for Hydrogen-assisted Cracking (Hydrogen Embrittlement),' Metallurgical Transactions, vol. 3, pp. 437-&, 1972. [42] E. Sirois and H. K. Birnbaum, 'Effects of Hydrogen and Carbon on Thermally Activated Deformation in Nickel,' Acta metallurgica et materialia, vol. 40, pp. 1377-1385, 1992. [43] G. M. Pressouyre and I. M. Bernstein, 'A Kinetic Trapping Model for Hydrogen-induced Cracking,' Acta Metallurgica, vol. 27, pp. 89-100, 1979. [44] G. M. Pressouyre, 'Trap Theory of Hydrogen Embrittlement,' Acta Metallurgica, vol. 28, pp. 895-911, 1980. [45] A. W. Thompson, 'Environment Sensitive Fracture of Engineering Materials,' TMS-AIME, p. 379, 1979. [46] T. Toh and W. M. Baldwin, Stress Corrosion Cracking and Embrittlement. New York: John Wiley & Sons, 1956. [47] J. D. Fast, Interaction of Metals and Gases: Thermodynamics and phase relations: Academic Press, 1965. [48] A. J. Kumnick and H. H. Johnson, 'Deep Trapping States for Hydrogen in Deformed Iron,' Acta Metallurgica, vol. 28, pp. 33-39, 1980. [49] D. P. Williams and H. G. Nelson, 'Embrattlement of 4130-steel by Low-pressure Gaseous Hydrogen,' Metallurgical Transactions, vol. 1, pp. 63-&, 1970. [50] J. K. Tien, et al., 'Hydrogen Transport by Dislocations,' Metallurgical Transactions a-Physical Metallurgy and Materials Science, vol. 7, pp. 821-829, 1976. [51] A. W. Thompson and I. M. Bernstein, 'Wet and Dry Removal of Tropospheric Formaldehyde at A Coastal Site,' Adv. Corros. Sci. Tech., vol. 7, pp. 53-175, 1980. [52] A. Saxena and S. J. Hudak, 'Evaluation of the 3-Component Model for Representing Wide-range Fatigue Crack Growth-rate Data,' Journal of Testing and Evaluation, vol. 8, pp. 113-118, 1980. [53] J. Newman, J. C., 'Stress Analysis of the Compact Specimen Including the Effects of Pin Loading,' presented at the Fracture Analysis (8th Conference), ASTM STP 560, ASTM, 1974. [54] J. E. Srawley, 'Wide Range Stress Intensity Factor Expressions for ASTM Method E399 Standard Fracture Toughness Specimens,' International Journal of Fracture, vol. 12, pp. 475-476, June 1976. [55] D. Thibault, et al., 'Reformed Austenite Transformation During Fatigue Crack Propagation of 13%Cr–4%Ni Stainless Steel,' Materials Science and Engineering: A, vol. 528, pp. 6519-6526, 2011. [56] E. Lorincz, et al., 'Interferometric Statistical Measurement of Surface-roughness,' Applied Optics, vol. 25, pp. 2778-2784, Aug 1986. [57] C. A. Depew and R. D. Weir, 'Surface Roughness Determination by Measurement of Reflectance,' Applied Optics, vol. 10, pp. 969-&, 1971. [58] K. P. Staudhammer, et al., 'Nucleation and Evolution of Strain-induced Martensitic (b.c.c.) Embryos and Substructure in Stainless Steel: A Transmission Electron Microscope Study,' Acta Metallurgica, vol. 31, pp. 267-274, 1983. [59] S. Onodera, et al., 'Effect of Crack-starter Bead Application on the Drop-weight NDT Temperature,' in Drop-Weight Test for Determination of Nil-Ductility Transition Temperature, User's Experience with ASTM Method E 208, J. M. Holt and P. P. Puzak, Eds., ed Fairfield, PA: ASTM, 1986, pp. 34-55. [60] G. E. Linnert, Welding Metallurgy: Fundamentals, 4th ed. vol. 1: American Welding Society, Miami, FL, 1994. [61] G. Birkbeck, et al., 'Aspects of Stage II Fatigue Crack Propagation in Low-carbon Steel,' Journal of Materials Science, vol. 6, pp. 319-323, 1971. [62] M. C. Young, et al., 'Corrosion Fatigue Behavior of Cold-Worked 304L Stainless Steel in a Simulated BWR Coolant Environment,' Materials Transactions, vol. 50, pp. 657-663, 2009. [63] G. A. Webster, 'High-temperature Fatigue Crack-growth in Superalloy Blade Materials,' Materials Science and Technology, vol. 3, pp. 716-725, Sep 1987. [64] R. Mittal, et al., 'Effect of Vibration Loading on the Fatigue Life of Part-through Notched Pipe,' International Journal of Pressure Vessels and Piping, vol. 88, pp. 415-422, 2011. | |
dc.identifier.uri | http://tdr.lib.ntu.edu.tw/jspui/handle/123456789/64564 | - |
dc.description.abstract | 本研究係針對核電廠常用的 316L不銹鋼與A508低合金鋼,進行以大氣為主之疲勞裂縫成長速率試驗,並探討不同熱處理或冷加工之差異性。實驗用316L不銹鋼試片包含:經過1050℃/ 20 min固溶處理之母材(316L-BM)試片、冷軋母材(316L-CR)、冷加工後敏化(316L-CRS)與1100℃/ 1 h晶粒粗大化(316L-CG)試片等。A508低合金鋼方面,主要有母材(A508-BM)、母材經900℃/ 1h固溶後水淬(A508-SQ)與淬火後621℃/ 24 h回火(A508-QT)等試片。上述316L與A508試件皆於空氣與氫氣中進行25℃與300℃之疲勞裂縫成長試驗,以探討氫脆效應對裂縫成長速率的影響。實驗結果顯示,25℃大氣下測試之316L試片中,冷加工與敏化熱處理對常溫之裂縫成長速率無明顯影響(316L-BM-25A、316L-CR-25A和316L-CRS-25A);而粗晶試片(316L-CG-25A)因差排移動受晶界阻礙減少,在高ΔK(應力強度因子範圍)區之裂縫成長速率有加速的情形。於空氣中300℃測試者,經敏化之試片(316L-CRS-300A)FCGR和冷輥試片(316L-CR-300A)相比無加速之現象;輥壓試片(316L-CR-300A)受應變誘發麻田散鐵強化,裂縫成長速率較未變態之母材試片(316L-BM-300A)低;及粗晶試片(316L-CG-300A)因粗糙度誘發裂縫閉合效應,速率和母材試片(316L-BM-300A)相當外,其他則與25℃大氣中試驗結果大致相同。另一方面,經不同熱處理的A508試片,在大氣中之疲勞裂縫成長行為並無明顯差異,300℃測試結果亦大致相同。上述試片於25℃氫氣中,則與大氣中有相當的改變,316L-BM-25H試片為316L四組試片中氫脆敏感性最低者,而A508淬火試片(A508-SQ-25H)則因麻田散鐵變態量高,其氫脆敏感性提升,裂縫成長速率較母材試片(A508-BM-25H)為快。整體而言,大氣中測試之316L和A508試片,其300℃之速率皆較25℃測試者為高,除材料於高溫塑性較佳,使裂縫成長較快外,316L於高溫測試過程中沒有無相變態誘發之裂縫閉合效應亦為原因之一。另一方面,雖然316L之敏化熱處理之效應不明顯,但於低溫氫環境下使用時,仍有裂縫成長加速現象,此係因氫原子隨差排移動至應力集中區,促進局部塑性變形,使應變誘發之麻田散鐵變態集中於裂縫尖端,而加速疲勞裂縫成長,此現象與氫促進局部塑性理論相符合。 | zh_TW |
dc.description.abstract | This study focused on two commonly used materials, 316L stainless steel and A508 low-alloy steel, in the nuclear power industry. In the fatigue tests, several differently treated 316L specimens were used: 20% cold rolled (316L-CR), cold rolled and sensitized (316L-CRS), grain-coarsened (316L-CG), and solution-treated base metal (316L-BM). The A508 steel was tested in three conditions including as-received (A508-BM), solution-treated and water-quenched (A508-SQ), and quenched and tempered (A508-QT). A series of fatigue crack growth rate (FCGR) tests was conducted at 25°C and in air 300°C, and the results were compared. The FCGR tests for various 316L and A508 specimens were also conducted in gaseous hydrogen at 25°C to investigate the influence of hydrogen embrittlement (HE). To identify the specimens tested at various conditions, the numbers (temperature) together with A (air) or H (hydrogen) were attached to the specimen's designation for simplicity. For instance, the 316L-CR-25H represented the 316L-CR specimen which was tested in hydrogen at 25°C. Experimental results revealed that the 316L-BM-25A, 316L-CR-25A and 316L-CRS-25A specimens had similar FCGRs, implying that cold-working and sensitization treatment had little influence on FCGRs in air at 25°C. Under the same condition, the 316L-CG-25A specimen exhibited higher FCGRs at high ΔK (stress intensity factor range), possibly due to fewer grain boundaries to retard the motion of dislocations. For specimens tested in air at 300°C, both the 316L-CR-300A and 316L-CRS-300A specimens possessed similar FCGRs. Due to the lack of strain-induced martensitic transformation at 300°C, the 316L-CR-300A specimens with pre-existing (alpha)' had higher strength / hardness and lower FCGRs than the 316L-BM-300A specimen. In addition, the 316L-CG-300A specimen had FCGRs close to that of the 316L-BM-300A specimen, possibly owing to the effect of roughness-induced crack closure. The FCGRsof the A508 specimens did not differ from each other significantly under various heat treatments and test temperatures (25°C and 300°C) in air. Nevertheless, the results of the 316L and A508 specimens tested in H2 at 25°C were remarkably different from those tested in air at 25°C. The 316L-BM-25H specimen had the lowest FCGR among the four groups of 316L specimens. Furthermore, the A508-SQ-25H specimen, with a greater amount of untempered martensite, possessed higher FCGRs than the A508-BM-25H specimen due to the effect of HE. In general, the average FCGR of a given 316L or A508 specimen tested at 300°C was higher than that at 25°C, owing to improved ductility at elevated temperatures. Aditionally, the absence of strain-induced martensitic transformation, i.e., no phase transformation-induced crack closure, could also contribute to the higher FCGRs of 316L specimens at 300°C. Although the sensitization is not apparent for 316L steel, the FCGRs of specimens tested at low temperatures in hydrogen were accelerated. This phenomenon is associated with strain-induced martensite formation at the crack’s front and agrees with the Hydrogen Enhanced Localized Plasticity (HELP) theory. | en |
dc.description.provenance | Made available in DSpace on 2021-06-16T17:54:50Z (GMT). No. of bitstreams: 1 ntu-101-R99527006-1.pdf: 23379052 bytes, checksum: e1793cf062c5922f659e41c91b8b3238 (MD5) Previous issue date: 2012 | en |
dc.description.tableofcontents | 口試委員會審定書 .................................................. i
誌謝 ..................................................................... ii 中文摘要 .............................................................. iii 英文摘要 .............................................................. iv 第一章 前言 ........................................................... 1 第二章 文獻回顧 ..................................................... 2 2.1 核電廠反應器及其材料簡介 ................................ 2 2.1.1 核能反應器分類及輕水式反應器簡介 ................ 2 2.1.2 壓力式及沸水式反應器 .................................... 2 2.1.3 反應器相關組件及材料選用 ............................. 4 2.2 麻田散鐵相變態與相關理論................................. 5 2.2.1 麻田散鐵晶體簡介........................................... 5 2.2.2 麻田散鐵變態溫度........................................... 7 2.2.3 應變誘發麻田散鐵相變態................................. 7 2.3 疲勞破壞現象與理論 ......................................... 7 2.3.1 疲勞與相關理論發展簡介 ................................ 7 2.3.2 疲勞裂縫成長機構 .......................................... 9 2.3.3 沃斯田鐵系不銹鋼之疲勞裂縫成長機構 ............ 12 2.3.4 疲勞裂縫閉合效應 ......................................... 12 2.4氫脆現象與相關理論 .......................................... 13 2.4.1氫脆機構簡介 ................................................. 15 2.4.2氫脆對金屬材料之影響..................................... 16 第三章 實驗設備與方法........................................... 22 3.1 實驗材料 ......................................................... 22 3.2 實驗材料前處理與流程 ...................................... 22 3.3 微硬度量測與金相觀察 ...................................... 25 3.4 疲勞試片製備與試驗方法 .................................. 27 3.5 疲勞斷面X-ray繞射相組成分析 ........................... 32 3.6 SEM顯微組織分析 ........................................... 32 3.7 肥粒鐵含量量測儀(ferriscope)分析 ................. 34 3.8 疲勞斷面粗糙度測定 ......................................... 34 第四章 結果與討論 ................................................. 37 4.1 經前處理母材顯微組織分析 ............................... 37 4.2 疲勞試驗結果 ................................................... 42 4.3 疲勞試片破壞表面之相分析 ............................... 61 4.4 疲勞試片破斷表面顯微組織分析 ......................... 66 第五章 結論 ........................................................... 83 第六章 參考文獻 ..................................................... 85 | |
dc.language.iso | zh-TW | |
dc.title | 316L與A508鋼材之疲勞裂縫特性研究 | zh_TW |
dc.title | The Study of Fatigue Crack Characteristics of 316L and A508 Steels | en |
dc.type | Thesis | |
dc.date.schoolyear | 100-2 | |
dc.description.degree | 碩士 | |
dc.contributor.coadvisor | 陳鈞(Chun Chen) | |
dc.contributor.oralexamcommittee | 蔡履文(Leu-Wen Tsay) | |
dc.subject.keyword | 316L不銹鋼,A508低合金鋼,應變誘發麻田散鐵相變態,疲勞裂縫成長速率,熱處理,冷加工,氫脆., | zh_TW |
dc.subject.keyword | 316L stainless steel,A508 steel,strain-induced martensitic transformation,fatigue crack growth rate,heat treatment,cold work,hydrogen embrittlement., | en |
dc.relation.page | 88 | |
dc.rights.note | 有償授權 | |
dc.date.accepted | 2012-08-13 | |
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 |
文件中的檔案:
檔案 | 大小 | 格式 | |
---|---|---|---|
ntu-101-1.pdf 目前未授權公開取用 | 22.83 MB | Adobe PDF |
系統中的文件,除了特別指名其著作權條款之外,均受到著作權保護,並且保留所有的權利。