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完整後設資料紀錄
DC 欄位 | 值 | 語言 |
---|---|---|
dc.contributor.advisor | 段維新(Wei-Hsing Tuan) | |
dc.contributor.author | Chang-Ju Ho | en |
dc.contributor.author | 何昌儒 | zh_TW |
dc.date.accessioned | 2021-06-13T07:48:42Z | - |
dc.date.available | 2005-07-30 | |
dc.date.copyright | 2005-07-30 | |
dc.date.issued | 2005 | |
dc.date.submitted | 2005-07-26 | |
dc.identifier.citation | [1] S.R. Choi, N.P. Bansal, “Mechanical behavior of zirconia/alumina composites,” Ceramics International 31 (2005) 39-46
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Erdogan, and P.F. Joseph, “Toughening of Ceramics by circumferential microcracking,” J. Am. Ceram. Soc., 72 (1989) 262. [10] K.T. Faber, and A.G. Evans, “Crack deflection processes – Ι. Theory,” Acta Metall., 31 (1983) 565. [11] M. Taya, S. Hayashi, A.S. Kobayashi, and H.S. Yoon, “Toughening of a particulate Reinforced Ceramic-matrix Composite by Thermal Residual Stress”, J. Am. Cerma. Soc., 73, 1382, (1990). [12] N. Claussen, “Fracture toughness of Al2O3 with an unstabilized ZrO2 dispersed phase,” J. Am. Cerma. Soc., 59 (1976) 49. [13] R.M. McMeeking and A.G. Evans, “Mechanics of transformation-tiughening in brittle mterials,” J. Am. Cerma. Soc., 65 (1982) 242. [14] A.G. Evans and R.M. Cannon, “Toughening of brittle solids by martensitic transformations,” Acta Metall., 31 (1983) 565. [15] N. Claussen, J. Steeb and R.F. Pabst, “Effect of induced microcracking on the fracture toughness of ceramics,” Ceramic Bulletin, 56 (1977) 559. [16] M. Rühle, Kraus, A. Strecker, and D. Weidelich, “In-situ observation of phase transformation in ZrO2-containing ceramics,” Advances in Ceramics, Science and Technology of ZirconiaⅡ. Ed. By N. Claussen, M. Rühle and A. H. Heuer, American Ceramic Society, Columbus, OH [12] (1985) 256. [17] E. Bischoff and M. Rühle, “Microcrack and transformation toughening of zirconia-containing alumina,” Advances in Ceramics, Vol. 24B, Science and Technology of ZirconiaⅢ. ed. By S. Somiya, N. Yamamoto, and H. Yanagida, American Ceramic Society, Westerville, OH (1988) 635. [18] M. Rühle, N. Claussen, and A.H. Heuer, “Transformation and microcrack toughening as complementary processes in ZrO2-toughened Al2O3,” J. Am. Ceram. Soc., 69 (1986) 195. [19] A.G. Evan and K.T. Faber, “Toughening of ceramics by circumferential microcracking,” J. Am. Cerma. Soc., 64 (1981) 394. [20] Y.S. Shin, Y.W. Rhee and S.J. Kang, “experimental evaluation of toughening mechanisms in alumina-zirconia composites,” J. Am. Cerma. Soc. 82 (1999) 1229. [21] F.P. Knudsen, “Dependence of Mechanical Strength of Brittle Polycrystalline Specimens on Porosity and Grain Size”. J. Am. Ceram. Soc., 42, 376, (1959). [22] B. Mussles, M. V. Swain and N. Claussen, “Dependence of Fracture Toughness of Alumina on Grain Size and Test Technique,” J. Am. Cerma. Soc., 65[11] (1982) 566-572. [23] S.T. Bemsion and B.R. Lawn, “Role of Interfaced Grain Bridging Fracture in the Crack-Resistance and strength Properties of Non-Transforming Ceramics,” Acta Metall., 37[10] (1989) 2659. [24] J.W. Edington, D.J. Rowcliffe and J.L. Henshall, “The Mechanical Properties of Silicon Nitride and Silicon Carbide:Ⅰ. Material and Strength,” Powder Metall. Int. 7 (1975) 82. [25] E. Ryshkewitch, “Compression Strength of Porous Sintered Alumina and Zirconia,” J. Am. Ceram. Soc., 36 (1953) 65. [26] W. Duckworth, “Discussion of Ryshkewitch Paper,” J. Am. Ceram. Soc. 36 (1953) 68. [27] J.B. Wachtman, “Mechanical Properties of Ceramics: An Introductory Surbey ,” Am. Ceram. Soc. 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Metal Powder Industries Federation,” Princeton, New Jersey, U.S.A. (1994) appendix c [37] J.D. Achenbach, “Wave propagation in elastic solids,” American Elsevi Pub. Co., (1973). [38] M.J. Verkerk, A.J.A. Winnubst, A.J. Burggraaf, “Effect of impurities on sintering and conductivity of yttria-stabilized zirconia,“ J. Mater. Sci. 17, 3113-3122 (1982) [39] Pinggen Rao, Mikio Iwasa, Jianqing Wu, Jiandong Ye, Yingjun Wang, “Effect of Al2O3 addition on ZrO2 phase composition in the Al2O3-ZrO2 system,” Ceramics International 30 (2004) 923-926 [40] Wenjea J. Tseng, Masahiko Taniguchi and Toshiyuki, “Transformation strengthening of as-fired zirconia ceramics,” Ceramics International 25 (1999) 545-550 [41] Bikramjit Basu, Jef Vleugels, Omer Van der Biest, “Toughness tailoring of yttria-doped zirconia ceramics,”J. Mater. Sci. A 380 (2004) 215-221 [42] Laurence Ruiz, Michael J. Readey, “Effect of Heat Treatment on Grain Size, Phase Assemblage, and Mechanical Properties of 3 mol% Y-TZP,” J. Am. Ceram. Soc. 79 [9] 2331-2340 (1996) [43] A. Kuzjukevics, S. Linderoth, “Interation of NiO with yttria-stabilized zirconia,” Solid State Ionics 93 (1997) 255-261 [44] S. Chen, W. Deng and P. Shen, “Stablility of cubic ZrO2 (10mol.%Y2O3) when alloyed with NiO, Al2O3 or TiO2 : implications to solid electrolytes and cermets,” Mater. Sci. Eng. B22 (1994) 247 [45] Zhen-Yen Deng, Jian-Feng Yang, Yoshihisa Beppu, Motohide Ando, and Tatsuki Ohji, “Effect of Agglomeration on Mechanical Properties of Porous Zirconia Fabricated by Partial Sintering,” J. Am. Ceram. Soc., 85 [8] 1961-65 (2002) | |
dc.identifier.uri | http://tdr.lib.ntu.edu.tw/jspui/handle/123456789/35954 | - |
dc.description.abstract | 陶瓷的機械性質可以經由添加金屬或陶瓷顆粒達到改善的效果,而強度的增加量與第二相的添加量息息相關。以往研究,第二相的添加量往往在5vol%以上,本研究在ZrO2中加入Al2O3或Ni,而添加量少於5vol%。
本研究以無壓燒結的方式製備複合材。ZrO2/Al2O3複合材分別在15000C (一階段式)及16000C (二階段式) 下燒結,ZrO2/Ni複合材則在16000C下燒結,採用二階段式燒結可避免試樣大量的變形。ZrO2/Al2O3複合材的相對密度皆在99%以上。但是ZrO2/Ni複合材的相對密度則隨著鎳添加量的不同而有所變動,本研究所使用的燒結氣氛有空氣或一氧化碳混合,燒結氣氛對ZrO2基複合材緻密化行為扮演重要的角色。 本研究以四點彎曲的方式量測撓曲強度。ZrO2/Al2O3複合材的強度並未隨著第二相添加量之增加而提升。而ZrO2/Ni複合材其強度隨著第二相添加量的增加而上升,但是在更高的鎳添加量下,強度呈現下降,強度變化的趨勢與密度有密切的關聯。本研究以單邊切槽法(SENB)的方式量測破壞韌性,得到的結果顯示與強度測試有相同的趨勢。ZrO2/Al2O3複合材之機械性質在16000C燒結溫度下較ZrO2/Ni複合材良好,但是ZrO2的機械性質在Ni微量添加下有所提升。依照微結構的觀察去計算晶粒的大小。氧化鋯基材的晶粒受微量氧化鋁及鎳的添加影響不大,機械性質亦沒有受到晶粒大小的影響。這可能是由於孔隙之作用太大的原因。 | zh_TW |
dc.description.abstract | The mechanical properties of ceramics can be enhanced by adding either metallic inclusions or ceramic particles. The extent of enhancement is closely related to the second phase content. In the present study, the amount of second phase added is lower than 5vol%. Two systems, ZrO2/Al2O3 and ZrO2/Ni composites are investigated.
Pressureless sintering technique was used to prepare the composites. The sintering temperature was 15000C (one-stage) and 16000C (two-stage) for ZrO2/Al2O3 system and 16000C for ZrO2/Ni system. The two-stage sintering technique provides better dimension control. The relative density of the ZrO2/Al2O3 composites after sintering is higher than 99%. But the relative density of ZrO2/Ni composites varies with the Ni content. The sintering atmosphere used in the present study, air vs. CO, may play an important role on the densification behavior of the composites. The flexural strength was determined by using the 4-point bending technique. The strength of ZrO2/Al2O3 composites does not increase when a small amount of Al2O3 is added. The strength of ZrO2/Ni system depends strongly on the Ni content. The strength variation of ZrO2/Ni composites corresponds closely to their density variation. The fracture toughness was determined by using the single-edge-notched beam method. The similar results were obtained as that for strength. The mechanical properties of ZrO2/Al2O3 composites sintered at 16000C are superior to those of the ZrO2/Ni composites sintered at 16000C. But there is an increase of strength in ZrO2/Ni system as a small amount of 0.17vol%, is added. From the microstructural observation, the grain size was determined. The addition of Al2O3 affects little on the size of ZrO2 matrix grains. However, the addition of Ni particles also affect little on the grain size of ZrO2. Nevertheless, the mechanical properties are not affected by the grain size. It may be due to that the mechanical properties are over-shadowed by the influence of porosity. | en |
dc.description.provenance | Made available in DSpace on 2021-06-13T07:48:42Z (GMT). No. of bitstreams: 1 ntu-94-R92527030-1.pdf: 3959673 bytes, checksum: e631de00d7e34a12d65b948ff75cbdf9 (MD5) Previous issue date: 2005 | en |
dc.description.tableofcontents | 目錄
第一章 前言 1 第二章 文獻回顧 2 2-1 氧化鋯簡介 2 2-2 陶瓷基複合材料 2 2-3 第二相添加量對複合材機械性質的影響 3 2-4 陶瓷複合材料之相關韌化機制 6 2-4-1 Crack-bridging韌化機制 6 2-4-2 Crack deflection韌化機制 9 2-4-3 殘留熱應力韌化機制 9 2-4-4 應力引致相變化韌化機制 11 2-4-5 微裂縫韌化機制 11 2-5 微結構對陶瓷複合材之機械性質的影響 15 2-6 奈米複合材概要 16 第三章 實驗流程 18 3-1 原始材料 18 3-2 ZrO2/Al2O3複合材 18 3-2-1 試樣製備 18 3-2-2 相鑑定 23 3-2-3 密度測試 23 3-2-4 機械性質測定 25 3-2-4-1 楊式模數量測 25 3-2-4-2 撓曲強度 26 3-2-4-3 破壞韌性 26 3-2-5 微結構觀察 27 3-2-5-1 破斷面觀察 27 3-2-5-2 研磨拋光面觀察 27 3-2-5-3 晶粒尺寸 28 3-3 ZrO2/Ni複合材 29 3-3-1 試片製備 29 3-3-2 相鑑定 30 3-3-3 鎳含量鑑定 30 3-3-4 密度測試 30 3-3-5 機械性質測試 31 3-3-6 微結構觀察 31 第四章 結果與討論 32 4-1 ZrO2/Al2O3複合材 32 4-1-1 相鑑定 32 4-1-2 氧化鋯微量添加Al2O3的緻密化行為 35 4-1-3 微結構觀察 39 4-1-4 機械性質 45 4-2 ZrO2/Ni複合材 50 4-2-1 相鑑定 50 4-2-2 氧化鋯微量添加Ni的緻密化行為 52 4-2-3微結構觀察 55 4-2-4 機械性質 59 4-3 綜合比較 63 4-3-1 緻密化行為的比較 63 4-3-2 撓曲強度的比較 63 4-3-3 破壞韌性的比較 64 第五章 結論與建議 65 參考文獻 67 表目錄 表3-1 本研究所使用氧化鋁及氧化鋯之粉末特性 20 表3-2 本研究所使用硝酸鎳之特性 21 表3-3 ZrO2/Al2O3複合材所使用組成之單位對照表 22 表3-4 氧化鋯、氧化鋁、鎳之材料常數及材料性質 24 表3-5 以ICP測試ZrO2/Ni粉末中鎳的含量 30 表4-1 ZrO2/Al2O3試樣的楊氏模數與Al2O3添加量之關係 45 圖目錄 圖2-1 ZrO2/ Al2O3複合材之(a)強度 (b)韌性與Al2O3添加量關係圖 4 圖2-2 ZrO2/ Ni複合材之(a)強度 (b)韌性與Ni添加量關係圖 5 圖2-3 ZrO2/ Ni複合材之強度、韌性與Ni添加量關係圖 6 圖2-4 金屬添加物形成crack-bridging韌化機制 7 圖2-5 (a) 球狀添加物在陶瓷基材中殘留熱應力的分布狀態(b) 裂縫在兩個張 應力區之間傳播時,受到殘留熱應力(壓應力)的抑制 13 圖2-6 (a) 位於裂縫造成彈應力區內的氧化鋯顆粒,受到應力引致產生相變化 (b) 微裂縫韌化機制示意圖 14 圖2-7 奈米複合材之微結構分類 17 圖2-8 奈米複合材以其組合方式的維度分類 17 圖3-1 燒結曲線: (a) 一階段式燒結至15000C (b) 二階段燒結至16000C 22 圖4-1 ZrO2/5vol%Al2O3粉末及燒結後試樣之XRD繞射圖 33 圖4-2 原始氧化鋯粉末以及經過混粉、球磨、過篩後的粉末,在270~320的繞射圖形 34 圖4-3 ZrO2/Al2O3試樣之相對密度與Al2O3含量關係圖 36 圖4-4 ZrO2/Al2O3試樣之收縮率與溫度關係圖 37 圖4-5 ZrO2/Al2O3試樣的緻密化速率與溫度關係圖 38 圖4-6 (a) ZrO2 (b) ZrO2/1vol%Al2O3 (c) ZrO2/3vol%Al2O3 (d) ZrO2/5vol%Al2O3 在15000C燒結試樣的破斷面微結構 39 圖4-7 (a) ZrO2 (b) ZrO2/1vol%Al2O3 (c) ZrO2/3vol%Al2O3 (d) ZrO2/5vol%Al2O3在16000C燒結試樣的破斷面微結構 40 圖4-8 (a) ZrO2 (b) ZrO2/2vol% Al2O3 (c) ZrO2/4vol% Al2O3 (d) ZrO2/5vol% Al2O3 在15000C燒結試樣經熱腐蝕後的拋光面觀察,箭頭所示為氧化鋁顆粒 42 圖4-9 (a) ZrO2 (b) ZrO2/1vol%Al2O3 (c) ZrO2/2vol% Al2O3 (d) ZrO2/5vol% Al2O3在16000C燒結試樣經熱腐蝕後的拋光面觀察,箭頭所示為氧化鋁顆粒 43 圖4-10 ZrO2/Al2O3試樣的晶粒大小對Al2O3含量之關係圖 44 圖4-11 在(a) ZrO2/5vol%Al2O3 15000C燒結 (b) ZrO2/1vol%Al2O3 16000C燒結試樣中,較大氧化鋯晶粒伴隨氧化鋁的存在 44 圖4-12 ZrO2/Al2O3試樣之撓曲強度與Al2O3含量關係圖 47 圖4-13 ZrO2/Al2O3試樣之破壞韌性對Al2O3含量關係圖 49 圖4-14 ZrO2/0.26vol%Ni粉末及燒結後試樣之XRD繞射圖 51 圖4-15 ZrO2/Ni試樣之相對密度與Ni含量關係圖 54 圖4-16 A. Kuzjukevics及S. Linderoth發現在15000C燒結的8YSZ-NiO試樣,其晶粒大小與NiO含量的關係 54 圖4-17 (a) ZrO2 (b) ZrO2/0.1vol%Ni (c) ZrO2/0.17vol%Ni (d) ZrO2/0.23vol%Ni 試樣的破斷面微結構 56 圖4-18 (a) ZrO2 (b) ZrO2/0.1vol%Ni (c) ZrO2/0.17vol%Ni (d) ZrO2/0.23vol%Ni 燒結試樣經熱腐蝕後的拋光面觀察 57 圖4-19 ZrO2/Ni試樣的晶粒大小對Ni含量之關係圖 58 圖4-20 在孔洞附近伴隨著較大晶粒,孔洞可能是原來鎳的所在位置(ZrO2/0.17vol%Ni試樣) 58 圖4-21 ZrO2/Ni試樣之楊氏模數與Ni含量關係圖 61 圖4-22 ZrO2/Ni試樣之撓曲強度與Ni含量關係圖 61 圖4-23 ZrO2/Ni試樣之破壞韌性與Ni含量關係圖 62 圖4-24 裂縫在(a)較高Ni添加量(b)較低Ni添加量的傳播路徑 62 | |
dc.language.iso | zh-TW | |
dc.title | 氧化鋯添加微量氧化鋁或鎳之機械性質 | zh_TW |
dc.title | Effects of a Small Amount Al2O3 or Ni Addition on the Mechanical Properties of ZrO2 | en |
dc.type | Thesis | |
dc.date.schoolyear | 93-2 | |
dc.description.degree | 碩士 | |
dc.contributor.oralexamcommittee | 謝宗霖,楊聰仁,黃啟祥,陳榮志 | |
dc.subject.keyword | 機械性質,氧化鋯,氧化鋁,鎳,複合材,撓曲強度,破壞韌性,燒結氣氛, | zh_TW |
dc.subject.keyword | mechanical property,ZrO2,Al2O3,Ni,composite,flexural strength,fracture toughness,sintering atmosphere, | en |
dc.relation.page | 71 | |
dc.rights.note | 有償授權 | |
dc.date.accepted | 2005-07-26 | |
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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