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完整後設資料紀錄
DC 欄位 | 值 | 語言 |
---|---|---|
dc.contributor.advisor | 黃坤祥(Kuen-Shyang Hwang) | |
dc.contributor.author | Po-Han Chen | en |
dc.contributor.author | 陳柏翰 | zh_TW |
dc.date.accessioned | 2021-06-08T04:18:06Z | - |
dc.date.copyright | 2010-07-28 | |
dc.date.issued | 2010 | |
dc.date.submitted | 2010-07-28 | |
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dc.identifier.uri | http://tdr.lib.ntu.edu.tw/jspui/handle/123456789/22451 | - |
dc.description.abstract | 摘要
17-4 PH射出成形不銹鋼因結合了良好的機械性質與抗腐蝕能力,已被廣泛的運用於航太工業與醫療市場。一般17-4 PH不銹鋼粉末均使用真空與氫氣燒結,這是因為在這些氣氛中可利用δ + γ 雙相燒結得到高密度與良好的抗腐蝕性。而本實驗欲提升17-4 PH射出成形件強度並降低製程成本,故以裂解氨為燒結氣氛;期望利用滲氮增加不銹鋼之強度,且裂解氨氣氛也常使用於一般的高溫連續爐中。此外,由於一般17-4 PH燒結後硬度超過25 HRC,不易整形或加工,故本實驗也調整17-4 PH成分期望在裂解氨中燒結後之材料,於固溶淬火後不致過硬不利整形、加工,但在時效之後仍可得到兼具高強度、高韌性和優良抗腐蝕性的不銹鋼。 實驗中先比較了17-4 PH在真空、氫氣與裂解氨氣氛下燒結緻密化行為、機械性質和抗腐蝕性,結果顯示,在1320℃真空與氫氣下燒結已可達97.0%理論密度,但裂解氨下燒結只有94.3%,此是因為在1320℃裂解氨燒結時δ-肥粒鐵比例只有38%,遠低於氫氣中之61%,而此問題可藉由提高燒結溫度至1350℃或添加1 wt% Mo而解決,兩者在高溫時之δ-肥粒鐵已可達56%或57%,燒結後有97%理論密度。 在比較1350℃各燒結工件機械性質方面,真空與氫氣試片經熱處理後,硬度、強度分別為37.6 HRC、1180 MPa與38.6 HRC、1040 MPa,遠低於裂解氨試片之45.7 HRC、1350MPa,但是氫氣或裂解氨試片在熱處理後延性與衝擊能分別只有4.3%、5.8J和2.5%、6.3J遠低於真空之7.8%、67J。在抗腐蝕性方面,真空與氫氣試片經熱處理後,重量損失為0.0032與0.0040 g/dm2/day,而裂解氨試片高達0.0160 g/dm2/day,此已超過MPIF規範(0.005 g/dm2/ day)。 實驗後半部嘗試藉由元素之添加與熱處理以改善材料性質。當17-4 PH添加1 wt% Ni並於裂解氨燒結後經固溶、時效後之硬度與強度分別為39.7 HRC與1365 MPa,且延性與衝擊能可達6.4%與43.6 J,而17-4 PH添加 15 wt% 316L於裂解氨燒結者,經固溶、深冷後時效之硬度與強度為36.6 HRC與1264 MP且延性與衝擊能可達12.2%與64.7 J,兩者強度皆高於17-4 PH於真空和氫氣下燒結數據,且延性皆達MPIF規範。在改善整形和加工性方面,17-4 PH添加1 wt% Ni或15 wt% 316L於裂解氨燒結後在固溶階段硬度、強度已可由17-4 PH之32.3 HRC、1052MPa分別降至25.4 HRC、1020MPa及21.5 HRC、934MPa,此已有利於在固溶階段對材料進一步整形和加工。而在抗腐蝕方面,17-4 PH添加1 wt% Ni於裂解氨燒結並經固溶、時效後之重量損失已降至0.0089 g/dm2/day;而添加15 wt% 316L之試片於裂解氨中燒結並經固溶、深冷後時效後之重量損失更降至 0.0044 g/dm2/day,已符合MPIF 0.005 g/dm2/ day之規範。 | zh_TW |
dc.description.abstract | Abstract
Metal injection molded (MIM) 17-4 PH stainless steels are wildly used in the aircraft and medical industries due to the good mechanical properties and corrosion resistance. The 17-4 PH stainless steel is typically sintered in the dual phase region of δ+ γ under vacuum or hydrogen. Since nitrogen provides solution strengthening and dissociated ammonia (DA) is widely used in continuous furnaces in the industry, the 17-4PH was sintered in DA in this study and its effect on mechanical properties and corrosion resistance was investigated. Results showed that when the 17-4 PH was sintered in vacuum or hydrogen at 1320℃, 97.0% density was achieved, higher than the 94.3% of that sintered in DA. This was because the amount of delta ferrite is about 61% in hydrogen but only 38% in DA. By increasing the sintering temperature to 1350℃ or adding 1 wt% Mo into 17-4 PH, the amount of delta ferrite increased to 56% and 57%, respectively. Thus, high sintered density was attained. Specimen sintered in DA at 1350℃ reached 45.7 HRC hardness and 1350 MPa tensile strength, which are much higher than those of sintered in vacuum and hydrogen at 1350℃. However, the elongation and impact energy of the specimen sintered in hydrogen or DA were very low, around 4% and 6J. The corrosion resistance of 17-4 PH sintered in DA was poor at a rate of 0.0160 g/dm2/day, which exceeded the MPIF limit. To improve the properties of the 17-4PH sintered in DA, 1 wt% Ni was added into 17-4 PH. A hardness of 39.7 HRC, a tensile strength of 1365 MPa, an elongation of 6.4%, and an impact energy of 43.6 J was attained after solutioning and aging treatment. On other hand, when 15 wt% 316L was added into 17-4PH, the hardness, tensile strength, elongation, and impact energy were 36.6 HRC, 1264 MPa, 12.2%, and 64.7J was attained after solutioning, cryogenic, and aging treatment. Both these two methods decreased the hardness after solution treatment to 25.4 and 21.5 HRC for the specimen added with 1 wt% Ni and 15 wt% 316L, respectively. This hardness range is good for machining. The corrosion resistance was also improved by adding Ni and 316L addition. The weight loss rates of the specimens with the addition of 1 wt% Ni and 15wt% 316L were decreased to 0.0089 and 0.0044 g/dm2/day, respectively, after heat treatment. Keywords: Metal injection molding, 17-4 PH stainless steel, aging treatment, cryogenic treatment | en |
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dc.description.tableofcontents | 目錄
摘要 i Abstract iv 目錄 vi 圖目錄 ix 表目錄 xvi 第一章 文獻回顧 1 1.1金屬粉末射出成形簡介 1 1.2 17-4 PH析出硬化型不銹鋼簡介 3 1.3 17-4 PH析出硬化型不銹鋼之熱處理程序 10 1.3.1不同熱處理溫度對17-4 PH性質的影響 12 1.3.2時效處理對17-4 PH結構影響及強化機制 13 1.4 17-4 PH析出硬化型不銹鋼之射出成形 17 1.4.1 17-4 PH射出成形件與鑄鍛件性質之比較 18 1.4.2不銹鋼粉末之製造 20 1.4.3熱脫脂條件對17-4 PH 射出成形件性質的影響 22 1.4.4燒結溫度對17-4 PH 射出成形件性質的影響 23 1.4.5燒結氣氛對17-4 PH 射出成形件性質的影響 24 1.4.6氮對不銹鋼之影響 26 1.4.7氫對鋼的影響 26 1.4.8夾雜物對17-4 PH 射出成形件性質的影響 27 1.4.9碳、氧含量及SiO2對粉末冶金不銹鋼的影響 28 1.4.10添加元素或化合物對不銹鋼之影響 30 1.5 金屬切削(Metal Cutting)的原理和機制 31 1.6 研究動機 33 第二章 實驗步驟 36 2.1實驗設計 36 2.2原料 36 2.2.1 基礎粉 37 2.2.2 黏結劑 37 2.3混合及混煉 37 2.4射出成形 41 2.5溶劑脫脂及熱脫脂 43 2.6燒結 44 2.7熱處理 45 2.8性質量測及分析 45 2.8.1燒結密度 45 2.8.2硬度 45 2.8.3抗拉強度及延性 46 2.8.4降伏強度 46 2.8.5衝擊試驗 46 2.8.6切削性試驗 47 2.8.7抗腐蝕性試驗 49 2.8.8鐵素體含量測定 51 2.8.9碳氧氮含量測定 51 2.8.10金相製備 51 2.8.11微結構分析 51 2.9實驗儀器 52 第三章 結果與討論 53 3.1熱脫脂氣氛對17-4 PH之影響 53 3.2燒結氣氛與溫度對17-4 PH之影響 55 3.2.1燒結氣氛與溫度對17-4 PH緻密化之影響 55 3.2.2燒結氣氛對17-4 PH機械性質之影響 61 3.2.3燒結氣氛對17-4 PH抗蝕性之影響 75 3.3 添加元素和合金粉對17-4 PH之影響 79 3.3.1 添加BCC穩定元素鉬對17-4 PH緻密化之影響 79 3.3.2 添加FCC穩定元素和合金對17-4 PH機械性質之影響 81 3.3.2.1 添加鎳對17-4 PH機械性質之影響 81 3.3.2.2 添加316L不銹鋼粉末對17-4 PH機械性質之影響 84 3.4 熱處理對17-4 PH機械性質之影響 88 3.4.1 真空固溶、時效對17-4 PH之影響 88 3.4.2 時效溫度對17-4 PH之影響 89 3.4.3 深冷處理對17-4 PH的影響 92 3.5綜合添加元素、合金和熱處理對17-4 PH之影響 97 3.5.1 綜合添加元素、合金和熱處理對17-4 PH機械性質之影響 99 3.5.2 綜合添加元素、合金與熱處理對17-4 PH抗腐蝕性之影響 101 3.5.3 綜合添加元素、合金和熱處理對17-4 PH切削性之影響 103 第四章 結論 111 第五章 未來工作 113 第六章 參考文獻 114 附錄 122 圖目錄 圖1- 1 金屬粉末射出成形之製程[2] 2 圖1- 2 17-4 PH之溫度-銅相圖 (碳含量為0.03%),在1050℃左右時銅有最高的固溶量 9 圖1- 3 一般之固溶,時效處理製程[5] 10 圖1- 4 鐵-銅相圖,銅在1040℃時的固溶量可接近6 wt% 11 圖1- 5 17-4 PH僅作固溶的TEM照片[8] (a)亮視野、(b) 和 (c) 暗視野、 (d) 相對繞射圖形、 (e)為 (d)圖形的解析,麻田散鐵呈板狀且有(211)微雙晶產生 15 圖1- 6 17-4 PH經時效後(480℃ 持溫1小時)達尖峰時效時的TEM照片[8] (a)亮視野、(b) 和(c) 析出相和基地的相對繞射圖形,此時母相麻田散鐵與析出富銅相有配位(coherent)關係 16 圖1- 7 17-4 PH經時效後(620℃ 持溫4小時)過時效時的TEM照片[8] (a)亮視野、(b)暗視野和(c)回復沃斯田鐵,回復沃斯田鐵傾向於銅粒子旁出析出 16 圖1- 8比較17-4 PH射出成形件和鑄件在室溫和高溫的機械性質[18] ,射出成形件機械性質較差的原因為內含許多細小孔洞 19 圖1- 9 17-4 PH射出成形件經熱均壓與否之金相差異[18](a)未經熱均壓之MIM試片、(b)經熱均壓後之MIM 試片,熱均壓後孔洞明顯減少 19 圖1- 10 (a)離心式法、(b)氣噴霧法和(c)水噴霧法[2,19] 21 圖1- 11為(a)離心式法、(b)氣噴霧法和(c)水噴霧法,所得之粉體形貌[2,19] 22 圖1- 12 17-4 PH於不同氣氛下燒結之收縮率[25] 25 圖1- 13 沃斯田鐵相晶界之孔洞擴散路徑(a)無δ-肥粒鐵、(b)有δ-肥粒鐵相 [25] 25 圖1- 14 (a)17-4 PH燒結1350℃ 1小時、(b)17-4 PH燒結1350℃ 1小時[24,48],韌窩中的顆粒為SiO2 28 圖1- 15 (a)未添加NiB之破斷面、(b)添加1wt% NiB之破斷面[48] 30 圖1- 16 鋁合金、銅合金、碳鋼和不銹鋼的熱傳導係數之差異[3] 32 圖1- 17 冷加工對不銹鋼與碳鋼加工硬化的影響[3] 33 圖1- 18 實驗目標 34 圖1- 19 本研究的實驗流程圖 35 圖2- 1 金屬射出成形流程 36 圖2- 2 17-4 PH不銹鋼粉末之外觀 39 圖2- 3 316L不銹鋼粉末之外觀 39 圖2- 4鉬粉之粉末外觀 40 圖2- 5 鎳粉之粉末外觀 40 圖2- 6硫化錳粉之粉末外觀 41 圖2- 7平板試片之尺寸 42 圖2- 8拉伸試棒之尺寸 42 圖2- 9 熱脫脂升溫曲線 43 圖2- 10射出成形工件之燒結曲線,真空爐為燒結後降溫至850℃後開風扇快速冷卻至室溫,氣氛爐則為燒結後爐冷至室溫 44 圖2- 11衝擊試驗所使用之試片尺寸 46 圖2- 12 立式加工機 47 圖2- 13切削時試片與夾具配置圖 48 圖2- 14 切削試片尺寸 48 圖2- 15 加工後試片,每個試片鑽20個盲孔 49 圖2- 16 典型極化曲線圖 50 圖3- 1於不同氣氛熱脫脂後之碳、氮和氧含量,在氫氣下之碳含量低於真空 53 圖3- 2於不同氣氛熱脫脂後在1320oC真空燒結試片之碳、氮和氧含量,顯示兩者數據已差異不大 54 圖3- 3 於不同氣氛熱脫脂後在1320oC真空燒結試片之密度,經燒結後密度相同 54 圖3- 4 於1320oC真空和氫氣燒結所得之密度,皆可達97%理論密度 56 圖3- 5 利用Thermal-Calc模擬17-4 PH於1320℃氫氣燒結時之相分率,δ-肥粒鐵有61% 56 圖3- 6利用Thermal-Calc模擬在1320℃下固相中可存在之氮含量,約為0.125 wt% 57 圖3- 7 利用Thermal-Calc模擬17-4 PH於1320℃裂解氨燒結時之相分率,δ-肥粒鐵只有38% 58 圖3- 8 利用高溫熱膨脹儀比較17-4 PH於氫氣和裂解氨燒結之情形,氫氣燒結時δ-肥粒鐵出現溫度比裂解氨低200℃ 58 圖3- 9 於不同燒結氣氛與溫度所得之密度,1320℃裂解氨燒結只有94%的理論密度但溫度升至1350℃密度已可達97% 59 圖3- 10 於不同燒結氣氛與溫度所得之顯微組織,溫度由1320℃升至1350℃真空與氫氣之試片中δ-肥粒鐵(箭頭所指處)比例明顯上升,且組織也粗化許多 60 圖3- 11 於不同氣氛燒結後之碳、氮和氧含量,1320℃裂解氨燒結後氮含量達0.148wt% 61 圖3- 12 於不同氣氛燒結後所對應之Ms溫度,裂解氨試片之Ms溫度比真空和氫氣試片低了50℃ 62 圖3- 13於不同氣氛燒結後之相分析,各試片皆為BCT或BCC結構 62 圖3- 14裂解氨燒結後試片表面之氮化鈮與氮化鉻形貌 63 圖3- 15於不同氣氛燒結並經熱處理後之硬度,裂解氨燒結後硬度達34.9 HRC,熱處理後高達45.7 HRC 64 圖3- 16於不同氣氛燒結並經熱處理後之強度,裂解氨燒結後強度達1117MPa,熱處理後高達1350MPa 65 圖3- 17氫氣燒結後經拉伸後之破斷面晶界處,可發現銅析出於晶界上 65 圖3- 18於不同氣氛燒結並經固溶後之顯微組織與微硬度值(a)真空、(b)氫氣和(c)裂解氨,裂解氨試片之麻田散鐵硬度達343 HV,且難以觀察到δ-肥粒鐵 66 圖3- 19於不同氣氛燒結並經熱處理後之延性,氫氣與裂解氨試片僅固溶階段可達10%,但燒結和時效階段都低於MPIF規範 68 圖3- 20 於不同氣氛燒結並經熱處理後之破斷面(a)真空、(b)氫氣和(c)裂解氨,只有真空燒結試片仍有部分韌窩組織 68 圖3- 21 於不同氣氛燒結並經熱處理後之顯微組織(a)真空、(b)氫氣和(c)裂解氨,真空與氫氣下燒結組織相當,均富含許多δ-肥粒鐵 70 圖3- 22 鐵氫相圖,高溫時δ-肥粒鐵可固溶之氫含量約10wppm 72 圖3- 23 於不同氣氛燒結並經熱處理後之衝擊能,氫氣與裂解氨試片於時效後衝擊能均降至個位數 73 圖3- 24 於不同氣氛燒結並經熱處理後之衝擊試片變形情況 73 圖3- 25 於不同氣氛燒結,經熱處理後之衝擊破斷面,各試片於固溶階段均富含大量韌窩組織,但時效後僅真空仍有部分韌窩組織存在 74 圖3- 26 17-4PH於尖峰時效時易提高氫脆敏感性之示意圖 75 圖3- 27 於不同氣氛燒結並經熱處理後之抗腐蝕測試,裂解氨試片之重量損失已超過MPIF規範 76 圖3- 28 於不同氣氛燒結並經熱處理後之極化曲線,裂解氨試片曲線和真空、氫氣相比偏右下方,且無鈍化反應 77 圖3- 29 於裂解氨燒結並經熱處理後之氮化鈮及氮化鉻形貌(a)燒結後、(b)熱處理後,熱處理後氮化鉻已明顯變得細小 78 圖3- 30利用Thermal-Calc模擬17-4 PH +1 wt% Mo 於1320℃裂解氨下燒結時之相比例,δ-肥粒鐵有57% 79 圖3- 31利用高溫熱膨脹儀比較17-4 PH和17-4 PH+1 wt% Mo於裂解氨下燒結之情形,添加1 wt% Mo時δ-肥粒鐵出現溫度可由1200℃降至1100℃ 80 圖3- 32 17-4 PH和17-4 PH+1 wt% Mo於1320℃裂解氨下燒結所得之密度,添加1 wt% Mo之試片已可達97%的理論密度 80 圖3- 33 添加不同Ni含量於裂解氨燒結並經熱處理後之硬度,當Ni添加量大於1 wt%在時效後硬度已低於MPIF規範 82 圖3- 34添加不同Ni含量於裂解氨燒結並經熱處理後之強度,當Ni添加量大於1 wt%在時效後強度已低於MPIF規範 83 圖3- 35 添加不同Ni含量於裂解氨燒結並經熱處理後之磁性相比例,隨Ni含量提高而下降,當Ni添加量達3 wt%時磁性相比例將接近0 83 圖3- 36添加不同Ni含量於裂解氨燒結並經熱處理後之延性,隨Ni含量提高而上升,且添加1 wt% Ni已可使材料達MPIF規範 84 圖3- 37添加不同316L含量於裂解氨燒結並經熱處理後之硬度,當316L添加量大於10 wt%在時效後硬度已低於MPIF規範 86 圖3- 38添加不同316L含量於裂解氨燒結並經熱處理後之強度,當316L添加量大於10 wt%在時效後強度已低於MPIF規範 86 圖3- 39添加不同316L含量於裂解氨燒結並經熱處理後之磁性相比例,隨316L含量提高而下降 87 圖3- 40添加不同316L含量於裂解氨燒結並經熱處理後之延性,隨316L含量提高而上升 87 圖3- 41於不同氣氛燒結並經真空熱處理後之衝擊能 ,氫氣與裂解氨試片在時效後衝擊能仍處於個位數 88 圖3- 42 於不同時效溫度所得之硬度,各試片在482℃可達最高值表示已達尖峰時效 89 圖3- 43 於不同時效溫度所得之強度,氫氣試片在530℃時效強度略高於482℃ 90 圖3- 44於不同時效溫度所得延性,各試片在482℃可達最低值,氫氣與裂解氨試片隨時效溫度變化而敏感變動 91 圖3- 45於不同時效溫度所得之衝擊能,各試片在482℃可達最低值,氫氣與裂解氨試片隨時效溫度變化而敏感變動 91 圖3- 46 17-4PH於過時效時氫脆敏感性將下降之示意圖 92 圖3- 47 添加不同沃斯田鐵穩定元素或合金含量,於裂解氨燒結並經固溶、深冷後時效之硬度變化(a)不同鎳、(b)不同316L含量 93 圖3- 48添加不同沃斯田鐵穩定元素或合金含量,於裂解氨燒結並經固溶、深冷後時效之強度變化(a)不同鎳、(b)不同316L含量 94 圖3- 49添加不同沃斯田鐵穩定元素或合金含量,於裂解氨燒結並經固溶、深冷後時效之延性變化(a)不同鎳、(b)不同316L含量 95 圖3- 50添加不同沃斯田鐵穩定元素或合金含量,於裂解氨燒結並經固溶、深冷後時效之磁性相比例變化(a)不同鎳、(b)不同316L含量 96 圖3- 51添加不同沃斯田鐵穩定元素或合金含量,於裂解氨燒結並經各別熱處理後之機械性質(a)硬度、(b)強度和(c)延性 97 圖3- 52添加不同沃斯田鐵穩定元素或合金含量,於裂解氨燒結並經各別熱處理後之衝擊能,添加Ni與316L衝擊能將大幅上升 101 圖3- 53 添加不同沃斯田鐵穩定元素或合金含量,於裂解氨燒結並經各別熱處理後之抗腐蝕測試,當添加15 wt% 31L經深冷再時效後已可達MPIF規範 102 圖3- 54添加不同沃斯田鐵穩定元素或合金含量,於裂解氨燒結並經各別熱處理後之極化曲線,當添加15 wt% 316L時有鈍化反應 103 圖3- 55 鑽頭刀具圖示,切削性評估以材料加工後鑽頭刃口(Cutting Edge) 外端磨耗距離作討論 104 圖3- 56 各材料加工後鑽頭破壞情形 105 圖3- 57各材料加工時之切屑形貌 106 圖3- 58 添加不同沃斯田鐵穩定元素或合金含量,於裂解氨燒結並經各別熱處理後之磁性相比例 107 圖3- 59 添加不同沃斯田鐵穩定元素或合金含量,於裂解氨燒結所對應之Ms溫度,當添加1wt% Ni 與15 wt% 316L時 Ms已經接近室溫 107 圖3- 60添加不同沃斯田鐵穩定元素或合金含量,於裂解氨燒結並經各別熱處理後之相分析,添加1 wt% Ni與15 wt% 316L沃斯田鐵峰值將上升,且15 wt% 316L在深冷後沃斯田鐵峰值將下降 108 圖3- 61 添加不同沃斯田鐵穩定元素或合金含量,於裂解氨燒結並經各別熱處理後之顯微組織 109 圖3- 62添加15 wt% 316L於裂解氨燒結經固溶、深冷後之切削性評估,經深冷後刃口磨耗由0.135降至0.105 110 圖3- 63添加15 wt% 316L於裂解氨燒結經固溶、深冷後之切屑形貌,切屑長度已比固溶階段短了許多,由30mm降至24mm 110 表目錄 表1- 1 析出硬化型不銹鋼之代表鋼種型號及成份[3] 4 表1- 2 析出硬化型不銹鋼所使用之強化相[3] 6 表1- 3 17-4 PH析出硬化型不銹鋼之成分[3] 7 表1- 4常見金屬蒸氣壓與溫度之關係[2] 8 表1- 5 17-4 PH時效熱處理條件[3] 11 表1- 6 17-4 PH鑄鍛件成品經不同熱處條件後所需最低機械性質[3] 13 表1- 7 17-4 PH 射出成形件之MPIF機械性質規範 17 表2- 1 17-4 PH、316L、鉬粉、鎳粉和硫化錳粉之化學組成與粉末特性 38 表2- 2粉末射出成形參數 41 表2- 3 切削參數[55] 48 表3- 1於不同氣氛燒結並經熱處理後腐蝕電位(E corr)和腐蝕電流密度(I corr) 77 表3- 2 17-4 PH添加不同Ni含量於1350℃裂解氨燒結時 之δ-肥粒鐵比例和燒結密度 81 表3- 3 17-4 PH添加不同316L含量於1350℃裂解氨燒結時 之δ-肥粒鐵比例和燒結密度 85 表3- 4 添加1 wt% Ni或15 wt% 316L所對應之成分 99 表3- 5 添加不同沃斯田鐵穩定元素或合金含量,於裂解氨燒結並經各別熱處理後之降伏強度 100 表3- 6 添加不同沃斯田鐵穩定元素或合金含量,於裂解氨燒結並經各別熱處理後之腐蝕電位(E corr)和腐蝕電流密度(I corr) 102 | |
dc.language.iso | zh-TW | |
dc.title | 金屬射出成形17-4 PH不鏽鋼之機械性質及加工性之改進 | zh_TW |
dc.title | Improvements in Mechanical Properties and Machinability of MIM 17-4 PH Stainless Steel | en |
dc.type | Thesis | |
dc.date.schoolyear | 98-2 | |
dc.description.degree | 碩士 | |
dc.contributor.oralexamcommittee | 陳鈞,林招松,陸永忠 | |
dc.subject.keyword | 金屬射出成形,17-4 PH不銹鋼金,屬射出成形,17-4 PH 不,銹鋼,時效處理,深冷,處理, | zh_TW |
dc.subject.keyword | Metal injection molding,17-4 PH stainless steel,aging treatment,cryogenic treatment, | en |
dc.relation.page | 127 | |
dc.rights.note | 未授權 | |
dc.date.accepted | 2010-07-28 | |
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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