TWI328018B - - Google Patents

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TWI328018B
TWI328018B TW94141746A TW94141746A TWI328018B TW I328018 B TWI328018 B TW I328018B TW 94141746 A TW94141746 A TW 94141746A TW 94141746 A TW94141746 A TW 94141746A TW I328018 B TWI328018 B TW I328018B
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carbon fiber
composite material
ceramic
resin
vapor
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TW94141746A
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Chinese (zh)
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TW200634073A (en
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Yukihiko Takahashi
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Showa Denko Kk
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1328018 (1) 九、發明說明 【發明所屬之技術領域】 本發明係關於含有碳材料及陶瓷之複合村料，組$ % ，其組成物與高分子材料或油類所成複合材料與g ^ 3 法，及使其複合材料進行成形加工所得，輕纛且導g彳生 異之成形體。 【先前技術】 近年，由於電子裝置高·性能化使得LSI (大規胃_ _ 電路）之微細化持續進行，今後LSI之洩漏電力（Uak power)已無法充分發揮LSI之性能。此時會成爲問題者 乃是L S I之發熱。在無法抑制發熱所致溫度上昇時則丨曳漏 電量進而增大，最惡之情形，會引起熱暴衝（thermal runaway ) 。 對此問題，係採用局部冷卻•放熱之放熱風扇或放熱 薄片。但是，隨著近年來電子裝置之小型化變得無法設置 放熱風扇，進而由於高密度化所伴隨發熱量之增加，在習 知之放熱薄片則無法進行充分地放熱。爲滿足該等要求， 可提高放熱薄片之放熱性者爲所求。 在放熱薄片方面，將習知之導熱性塡充劑分散於基質 樹脂中爲周知。在填充劑方面，由於在表面具有官能基而 所望量之充塡爲可行，故使用氧化鋁，氮化硼，氮化矽， 氮化鋁等。但是，因塡充劑本身之導熱率低，要提高放熱 薄片之導熱率則必須使塡充劑爲高充塡，而與放熱薄片之 -5- (2) (2)1328018 質量增加相關。因此’爲謀求減輕放熱薄片之質量，塡充 劑方面’充塡有輕質且導熱性優異之石墨微粉或者碳纖維 之放熱薄片則被檢討著。 在添加石墨微粉時’雖可獲得比陶瓷更爲導熱優異之 放熱薄片’但石墨微粉由於表面不具有官能基而與樹脂之 密接性差強度會降低。又，添加碳纖維及氣相法碳纖維者 ’由於流動性顯著惡化故無法爲高充塡，結果要獲得具有 充分導熱率之放熱薄片有所困難。 在日本特開平11-279406號公報，在聚矽氧橡膠基材 使瀝青（pitch)系之碳纖維分散以提高導熱率之方法被揭 示。然而，爲獲得實用上之導熱率，則會有多量配合瀝青 系碳纖維之必要的問題存在。日本特開2002-020 1 79號公 報’在呋喃樹脂等配合石墨微粉及氣相法碳纖維之高導熱 率複合材被揭示。 但是’由於石墨在表面幾乎不具官能基故無法進行高 充塡’雖可達成輕量化但要獲得充分導熱率有所困難。又 ’陶瓷與氣相法碳纖維之混合，以乾式之混合氣相法碳纖 維易於起毛球，分散於陶瓷及基質全體則有困難。 在添加長寬比大的氣相法碳纖維時流動性之惡化顯著 ’充塡份數變少結果會有無法獲得充分導熱率之問題。 又’陶瓷與氣相法碳纖維之混合，以乾式之混合氣相 法碳纖維易於起毛球，分散於陶瓷及基質全體有所困難。 在曰本特開2003- 1 1 90 1 9號公報藉由在陶瓷以偶合劑 或界面活性劑所致表面處理提高流動性者被揭示。但是， -6- (3) (3)1328018 藉由陶瓷之表面處理雖可改善流動性，但將原來導熱率低 的陶瓷成爲表面之物在作爲放熱材料使用之際，會使粒子 彼此之間之接觸電阻變大使得導熱率更降低，要獲得充分 導熱率有所困難。 因此’可提供輕量，且具有高導熱性之放熱風扇或放 熱薄片用途用之成形體用之材料開發被強烈企望。 【發明內容】 本發明之課題係提供一種輕量且具有高導熱性之放熱 風扇或放熱薄片用之成形體及其成形體用之材料。 本發明係關於，以下所示複合材料用組成物，使用該 組成物之複合材料，其製造方法，及成形體。 1.一種複合材料用組成物’其特徵爲含有碳材料及陶 瓷。 2·如申請專利範圍第1項記載之複合材料用組成物， 其中碳材料係選自碳纖維，焦炭粉及石墨粉所成群之至少 —種° 3. 如申請專利範圍第2項記載之複合材料用組成物， 其中碳纖維係氣相法碳纖維或碳奈米管。 4. 如申請專利範圍第3項記載之複合材料用組成物， 其中氣相法碳纖維係平均纖維徑50〜500nrn，長寬比5〜 1 〇〇〇之氣相法碳纖維。 5·如申請專利範圍第4項記載之複合材料用組成物 ’其中平均纖維徑50〜500nm，長寬比5以μ a 不足40之 (4) 1328018 氣相法碳纖維係分散於陶瓷粉體中。 • 6.如申請專利範_ 1項記載之複合材料用組成物， 其中陶瓷係選自氧化鋁，氧化鎂，氧化鋅’二氧化矽及薄 化硼所成群之至少一種之化合物。 7·如申請專利範圍第！項記載之複合材料用組成物， 其中陶瓷係平均粒子徑〇·3〜80_，比表面積〇 〇1〜 Un^/g之陶瓷粒子 • 8.如申請專利範圍第1項記載之複合材料用組成物’ 其中碳材料係氣相法碳纖維.，陶瓷係氧化鋁或氣化硼 9. 如申請專利範圍第4項記載之複合材料用組成物 ’其含有平均纖維徑1〇〜5〇〇nm ’長寬比5〜1〇〇〇之氣相 法碳纖維及陶瓷粒子，在該氣相法碳纖維及該陶瓷粒子透 過具有黏接性之高分子化合物，在該陶瓷粒子之表面之至 少一部份附著該氣相法碳纖維。 10. 如申請專利範圍第9項記載之複合材料用組成物 • ’其中高分子化合物係選自苯酚樹脂，聚乙烯醇樹脂，呋 喃樹脂，纖維素樹脂，聚苯乙烯樹脂，聚醯亞胺樹脂，及 . 環氧基樹脂所成群之至少一種。 • 11.如申請專利範圍第9項記載之複合材料用組成物 ，其中高分子化合物之配合量相對於陶瓷及氣相法碳纖維 之總量爲0.1〜30質量％。 12. 如申請專利範圍第1項記載之複合材料用組成物 ’其中碳材料之配合量爲陶瓷配合量之…丨〜刊質量％。 13. —種複合材料，其特徵爲在如申請專利範圍第1 (5) 1328018 項記載之組成物配合高分子材料或油類者。 14.如申請專利範圍第1 3項記載之複合材料，其含 _ 有平均纖維徑10〜500nm，長寬比5〜1000之氣相法碳纖 維及陶瓷粒子’在該氣相法碳纖維及該陶瓷粒子透過具有 黏接性之局分子化合物’在該陶瓷粒子之表面之至少一部 份附著該氣相法碳纖維之複合材料用組成物配合高分子材 料或油類。 • 15 _如申請專利範圍第1 3項記載之複合材料，其中 局分子材料或油類係選自脂肪族系樹脂，不飽和聚醋樹脂 ’丙烯酸樹脂，甲基丙烯酸樹脂’乙烯酯樹脂，環氧基樹 脂，聚砂氧樹脂，聚砂氧油，石油系油，及氟系油所成群 之至少一種。 1 6 _如申請專利範圍第1 3項記載之複合材料，其中 高分子材料或油類之配合量爲碳材料及陶瓷合計量之1〜 3 5質量％。 B 17.—種成形體，其爲如申請專利範圍第13項記載之 複合材料所成。 18.如申請專利範圍第17項記載之成形體，其爲薄片 ' 狀或薄膜狀。 - 19. 一種放熱薄片，其特徵爲使用如申請專利範圍第 . 1 8項記載之成形體。 20. —種個人電腦，其爲使用如申請專利範圍第19項 記載之放熱薄片。 21. —種遊戲機，其爲使用如申請專利範圍第19項記 -9 - (6) (6)1328018 載之放熱薄片。 22.—種數位攝影機’其爲使用如申請專利範圍第19 項記載之放熱薄片。 23 . —種數位相機，其爲使用如申請專利範圍第1 9項 記載之放熱薄片。 24.—種電視其特徵爲使用如申請專利範圍第1 9項記 載之放熱薄片。 25 · —種攜帶電話，其特徵爲使用如申請專利範圍第 1 9項記載之放熱薄片。 26. 如申請專利範圍第13項記載之複合材料之製造方 法’其爲將碳材料及陶瓷以乾式剪斷攪拌，將所得之組成 物分散於高分子材料或油類。 27. 如申請專利範圍第14項記載之複合材料之製造方 法，其中相對於平均纖維徑10〜500nm，長寬比5〜1〇〇〇 之氣相法碳纖維及陶瓷粒子係使用具有黏接性之高分子化 合物將該氣相法碳纖維複合化於陶瓷粒子表面，使所得組 成物分散於高分子材料或油類者 本發明之複合材料用組成物，含有表面具有官能基之 陶瓷’且與該陶瓷比較含有輕量且導熱性高的碳材料，與 作爲塡充劑之僅使用同量陶瓷之情形比較，在賦與複合材 料相同導熱性之際之添加量以少量即可，可使複合材料輕 量化。一方面’將作爲塡充劑僅爲同量之碳材料予以捏合 之情形相比較，因含有表面具有官能基之陶瓷故可充塡更 多’可使複合材料成爲更高之導熱性》 -10· (7) (7)1328018 又，作爲添加之陶瓷可適宜選擇密度小者，可維持一 定導熱率同時更爲輕量化。在添加之碳材料可適宜選擇導 熱率高者，可維持一定之質量同時可進行更高導熱率化。 此種組成物與高分子材料或油類所成本發明之複合材 料，在習知之複合材料並無法達成，而爲輕量且具有高導 熱性者。 接著，將此複合材料成形加工所得本發明之成形體亦 爲輕量且具有高導熱性，因爲放熱性優異，故可恰當地使 用於近年來因電子裝置或電·子零件之高性能化而成爲問題 ，爲了抑制LSI之發熱所致溫度上昇之放熱薄片或放熱薄 膜。 實施發明之最佳型態 本發明之複合材料用組成物含有碳材料及陶瓷。 碳材料方面，可使用選自氣相法碳纖維（導熱率400 〜1200w/(m.k))，碳奈米管（導熱率400〜1200w/( m · k ))，瀝青系或pan系之碳纖維（導熱率 200〜 lOOOw/ (m，k))等之碳纖維，焦炭粉（導熱率1〇〇〜 200w/ ( m · k ))，石墨粉（導熱率 100 〜200w/(m.k) )所成群之至少一種。 該等中以，導熱率優異之碳纖維爲佳，其中以具有更 高導熱性之氣相法碳纖維或碳奈米管爲佳。又，在成爲複 $材料之際，就可均一地分散於高分子材料或油類中之觀 點而言，比表面積小的氣相法碳纖維更佳（氣相法碳纖維 -11 - (8) 1328018 之比表面積1〇〜20m2/g，碳奈米管之比表面積200〜 * 3 00m2/g )。 ' 碳材料方面在使用氣相法碳纖維之情形，其平均纖維 徑以50〜500nm爲佳，更佳爲70〜3〇〇nm，進而較佳爲 80〜200nm，特佳爲 100〜I50nm。平均纖維徑不足 50nm 時處理性降低，平均纖維徑超過50〇nm時長寬比變小使得 導熱率降低。 φ 氣相法碳纖維之長寬比以5〜1000爲佳，更佳爲10〜 500，進而較佳爲15〜150，·特佳爲20〜120。長寬比爲5 以上時，導熱率提高效果大，長寬比爲1 000以下時則處 理性良好。 進而，藉由使使用之氣相法碳纖維之長寬比爲5以上 不足40，可提高在複合材料中之複合材料用組成物之流動 性，與添加長寬比40以上之氣相法碳纖維之情形比較導 熱率並不降低，且其黏度在更小的範圍。 φ 具體言之，陶瓷係使用氧化鋁之本發明複合材料之導 熱率爲1.6(W/(m.K))以上’且其黏度在丨(^口爪爲2〇 • (Pa.s)以下，在l〇〇rpm爲30(Pa.s)以下。又，陶 • 瓷係使用氮化硼之情形’爲2.0 ( W/ ( m · κ ))以上，更 佳爲 2.5(W/(m*K))，進而較佳爲 2.8(W/(m.K) )以上，且其黏度在l〇rp經爲30 ( pa · s )以下，在 lOOrpm 爲 40(Pa.s)以下。 更佳之長寬比爲1〇〜39，進而較佳爲15〜38，特佳 爲20〜38。 -12- (9) (9)1328018 上述碳材料，均可使用市售之物。又，關於製造方法 因有各種周知文獻存在，可依照該等來製造β 在氣相法碳纖維之情形，係將爲原料之苯等有機化合 物，與作爲觸媒之二茂鐵（ferrocene)等之有機過渡金屬 化合物一起，使用載體氣體導入於高溫反應爐，可進行氣 相熱分解來製造。製造方法方面，例如在基板上使熱分解 碳纖維生成之方法（日本特開昭60-27700號公報），在 浮遊狀態使熱分解碳纖維生成之方法（日本特開昭 60-5499 8號公報），在反應爐'壁使熱分解碳纖維成長之方法 (日本專利第2778434號公報）等，本發明所使用之碳纖 維可以該等方法來製造。 如此所製造之氣相法碳纖維，可照樣作爲原料使用， 但在氣相成長後之原樣狀態，會有表面來自原料之有機化 合物等之熱分解物或爲附著，或形成碳纖維之纖維構造之 結晶性不充分之情形。因此，爲將熱分解物等之不純物除 去，提高作爲碳纖維之結晶構造，則可在惰性氣體氛圍下 進行熱處理。爲處理來自原料之熱分解物等之不純物，則 在氬等之惰性氣體中進行約800〜15 00°C之熱處理爲佳。 又，爲提高碳構造之結晶性，則在氬等之惰性氣體中以進 行約2000〜3 000 °C之熱處理爲佳。以如此方式處理之氣相 法碳纖維，係以例如VGCF (登記商標：昭和電工公司製 )在市面販售。 碳材料係使用碳奈米管之情形’其平均纖維徑以3〜 50nm爲佳，更佳爲 3〜40nm’進而較佳爲 3〜30nm’特 -13- (10) (10)1328018 佳爲3〜20nm。纖維長以2〜20μηι爲佳，更佳爲5〜15μιη ’進而較佳爲6〜13μπι，特佳爲8〜12μπι。本發明所使用 之碳奈米管可使用一般市售之物，又如既存之多數文獻之 記載，若爲熟習該項技藝人士則爲可容易合成者。 本發明使用之陶瓷，係均一地分散於成爲複合材料基 質之高分子材料或油類。較佳爲選自氧化鋁、氧化鎂、氮 化矽、氮化硼、氮化鋁所成群之至少一種。其中以，與高 分子材料或油類之親和力佳，因成形容易，在成形過程氣 泡等難以混入，故以氮化硼、氧化鋁及/或氧化鎂更佳。 熱膨張率因氮化硼爲lxl〇_0/°C，氧化鋁爲 6xl(T6/°C，氧 化鎂爲14x1 (T6/°C，氮化硼及氧化鋁與其他塡充劑比較因 熱所致體積變化少，可減輕與高分子材料或油類之界面中 剝離。因此，本發明所用之陶瓷方面，尤以氧化鋁爲佳。 本發明所用之陶瓷以平均粒子徑0.3〜80μιη之粒子爲 佳，0.5〜70μιη者進而爲佳。平均粒子徑爲0·3μιη以上時 ，處理性良好，平均粒子徑爲8 0μιη以下時，並不會使強 度降低，進而可保持平面平滑性。又，以氮吸附法（BET 法）測定之比表面積以〇_〇1〜15m2/g爲佳’ 0.01〜10m2/g 進而爲佳。比表面積0.01 m2/g以上時可抑制強度之降低， 比表面積爲15m2/g以下時，可抑制陶瓷充塡量之減少。 本發明之組成物中，碳材料之配合量以陶瓷配合量之 0.1〜20質量％爲佳。進而較佳爲〇·5〜10質量％’特佳爲 0.8〜8質量％。碳材料之配合量爲質量％以上時’可 獲得導熱效果，又爲20質量％以下時，處理性爲良好。 -14 - (11) 1328018 碳材料與陶瓷之混合方法並無特別限定，但，碳材料 係使用碳纖維，尤以使用氣相法碳纖維之情形可使用 . Henschel硏磨機，球磨機或噴射硏磨機等在短時間施予剪 斷力予以混合爲佳。藉由施予剪斷力而混合，可使具有三 次元立體構造之氣相法碳纖維之全體或一部份被解開，在 與高分子材料或油類混合之際可行高分散。 本發明所使用之高分子化合物，係在氣相法碳纖維及 φ 陶瓷粒子具有黏接性之聚合物。所謂具有黏接性之高分子 化合物，係爲使陶瓷與氣相·法碳纖維以不分離之方式成爲 接觸狀態以介在該兩物體間進行共價鍵結，以凡得瓦爾力 、氫鍵等之化學黏接成爲使兩物體一體化之狀態者。在混 合、攪拌 '溶劑除去、熱處理等中，在使氣相法碳纖維之 剝離，脫落實質上不發生之程度相對於壓縮、彎曲 '剝離 、衝擊 '拉伸、撕裂等之力則顯示抵抗力時可適用作爲具 ♦ .. &gt; 有黏接性之高分子化合物。 # 例如’高分子化合物方面，可爲選自苯酚樹脂、聚乙 烯醇樹脂、呋喃樹脂、纖維素樹脂、聚苯乙烯樹脂、聚醯 .亞胺樹脂、環氧基樹脂所成群之至少一種。較佳爲苯酚樹 .· 脂、聚乙烯醇’進而較佳爲苯酚樹脂。尤以，使用混合乾 性油或其脂肪酸之苯酚樹脂可獲得更爲緻密的黏接性之複 合材料。此係’苯酚樹脂與乾性油中之不飽和鍵部分產生 化學反應’成爲所謂乾性油改性苯酚樹脂，而被推測其在 硬化過程中因分解緩和，可防止發泡之故。又，乾性油非 僅可謂單爲雙鍵*而爲具有相當長的烷基及酯鍵，該等被 -15- (12) (12)1328018 (1) IX. Description of the invention [Technical field to which the invention pertains] The present invention relates to a composite material containing carbon materials and ceramics, a group of %, a composite material thereof and a polymer material or an oil compound and g ^ 3 method, and the composite material obtained by forming the composite material, which is lightly smeared and leads to a different shape. [Prior Art] In recent years, the LSI (Ultra-regular __ circuit) has been continuously refined due to the high performance and performance of the electronic device. In the future, the LSI leakage power (Uak power) cannot fully utilize the performance of the LSI. It will become a problem at this time, but it is the fever of L S I. When the temperature rise due to heat generation cannot be suppressed, the amount of leakage current increases, and the worst case causes a thermal runaway. For this problem, a partial cooling/heat release exothermic fan or exothermic sheet is used. However, with the recent miniaturization of electronic devices, it has become impossible to provide an exhaust fan, and the heat radiation accompanying the increase in density has not been sufficiently radiated in the conventional heat-dissipating sheet. In order to satisfy these requirements, it is desirable to increase the heat release property of the exothermic sheet. In the case of an exothermic sheet, it is known to disperse a conventional thermal conductive agent in a matrix resin. In terms of a filler, alumina, boron nitride, tantalum nitride, aluminum nitride or the like is used because it is possible to have a sufficient amount of functional groups on the surface. However, since the thermal conductivity of the ruthenium itself is low, in order to increase the thermal conductivity of the exothermic sheet, the ruthenium must be highly charged, which is associated with an increase in the mass of the -5-(2) (2) 1328018 of the exothermic sheet. Therefore, in order to reduce the quality of the exothermic sheet, the graphite micropowder or the heat-dissipating sheet of carbon fiber which is excellent in lightness and thermal conductivity is reviewed. When the graphite fine powder is added, an exothermic sheet which is more excellent in thermal conductivity than ceramic is obtained. However, the graphite fine powder has a poor adhesion strength to the resin because the surface does not have a functional group. Further, since the carbon fiber and the vapor-phase carbon fiber are added, the fluidity is remarkably deteriorated, so that it is not sufficiently charged, and as a result, it is difficult to obtain a heat-releasing sheet having a sufficient thermal conductivity. Japanese Laid-Open Patent Publication No. Hei 11-279406 discloses a method of dispersing pitch carbon fibers in a polyoxyxene rubber substrate to increase the thermal conductivity. However, in order to obtain a practical thermal conductivity, there is a problem that a large amount of the pitch-based carbon fiber is necessary. Japanese Laid-Open Patent Publication No. 2002-020 1 79 discloses a high thermal conductivity composite material in which a fine powder of a furan resin or the like is mixed with a graphite fine powder and a vapor-phase carbon fiber. However, since graphite has almost no functional groups on the surface, it is impossible to carry out high filling. Although weight reduction can be achieved, it is difficult to obtain sufficient thermal conductivity. In addition, the mixing of ceramic and vapor-phase carbon fibers makes it difficult to pilling the carbon fibers in a dry mixed gas phase method, and it is difficult to disperse them in the ceramics and the matrix. When the gas-phase carbon fiber having a large aspect ratio is added, the deterioration of fluidity is remarkable. When the number of parts is small, there is a problem that sufficient thermal conductivity cannot be obtained. In addition, the mixing of ceramics and gas-phase carbon fibers is a dry-mixing method in which the carbon fibers are easy to pilling, and it is difficult to disperse in the ceramics and the matrix. It is disclosed in Japanese Patent Laid-Open Publication No. 2003- 1 1 90 1 9 by surface treatment of a ceramic with a coupling agent or a surfactant to improve fluidity. However, -6- (3) (3) 1328018 can improve the fluidity by the surface treatment of ceramics, but the ceramics with low thermal conductivity can be used as surface materials when they are used as exothermic materials. The contact resistance becomes large, so that the thermal conductivity is further lowered, and it is difficult to obtain sufficient thermal conductivity. Therefore, development of a material for a molded body for use in an exothermic fan or a heat-dissipating sheet which is lightweight and has a high thermal conductivity is strongly desired. SUMMARY OF THE INVENTION An object of the present invention is to provide a heat-generating fan or a molded body for a heat-releasing sheet which is lightweight and has high thermal conductivity, and a material for a molded body thereof. The present invention relates to a composition for a composite material shown below, a composite material using the composition, a method for producing the same, and a molded body. A composition for a composite material characterized by containing a carbon material and a ceramic. 2. The composite material composition according to the first aspect of the invention, wherein the carbon material is selected from the group consisting of carbon fiber, coke powder and graphite powder. 3. The compound as recited in claim 2 A composition for materials, wherein the carbon fiber is a gas phase carbon fiber or a carbon nanotube. 4. The composite material composition according to claim 3, wherein the vapor-phase carbon fiber is a vapor-phase carbon fiber having an average fiber diameter of 50 to 500 nrn and an aspect ratio of 5 to 1 Å. 5. The composite material composition as described in claim 4, wherein the average fiber diameter is 50 to 500 nm, and the aspect ratio 5 is μ a less than 40 (4) 1328018. The vapor-phase carbon fiber is dispersed in the ceramic powder. . 6. The composition for a composite material according to claim 1, wherein the ceramic is selected from the group consisting of at least one of alumina, magnesia, zinc oxide, cerium oxide, and thinned boron. 7. If you apply for a patent scope! The composition for a composite material according to the item, wherein the ceramic has an average particle diameter of 33 to 80 Å, and a ceramic particle having a specific surface area of 〇〇1 to Un^/g. 8. The composition for composite materials as recited in claim 1 The carbon material is a vapor-based carbon fiber. The ceramic-based alumina or the vaporized boron is 9. The composition for a composite material as described in claim 4 of the patent application has an average fiber diameter of 1 〇 5 5 nm. a vapor-phase carbon fiber and a ceramic particle having an aspect ratio of 5 to 1 Å, wherein the vapor-phase carbon fiber and the ceramic particle pass through a polymer compound having adhesion and adhere to at least a portion of a surface of the ceramic particle The gas phase carbon fiber. 10. The composition for a composite material according to claim 9 of the patent application. 'The polymer compound is selected from the group consisting of a phenol resin, a polyvinyl alcohol resin, a furan resin, a cellulose resin, a polystyrene resin, and a polyimide resin. And at least one of the group of epoxy resins. 11. The composition for a composite material according to claim 9, wherein the amount of the polymer compound is 0.1 to 30% by mass based on the total amount of the ceramic and the vapor-phase carbon fiber. 12. The composition for a composite material as recited in claim 1 wherein the amount of the carbon material is the amount of the ceramic compounding amount. A composite material characterized by blending a polymer material or an oil with a composition as recited in claim 1 (5) 1328018. 14. The composite material according to claim 13 which contains a gas phase carbon fiber having an average fiber diameter of 10 to 500 nm and an aspect ratio of 5 to 1000 and ceramic particles in the vapor phase carbon fiber and the ceramic The particles are bonded to the polymer composition or the oil by the composition of the composite material in which the gas phase carbon fiber is adhered to at least a part of the surface of the ceramic particle through the localized molecular compound having adhesiveness. • 15 _ As claimed in the patent application, item 13 of the composite material, wherein the molecular material or oil is selected from the group consisting of aliphatic resin, unsaturated polyester resin 'acrylic resin, methacrylic resin' vinyl ester resin, ring At least one of a group of an oxy resin, a polyoxyn resin, a polysand oil, a petroleum oil, and a fluorine-based oil. 1 6 _ The composite material as described in claim 13 of the patent application, wherein the blending amount of the polymer material or the oil is 1 to 35 mass% of the total amount of the carbon material and the ceramic. B 17. A molded body obtained by the composite material as recited in claim 13 of the patent application. 18. The molded article according to claim 17, which is in the form of a sheet or a film. 19. An exothermic sheet characterized by using the shaped body as described in claim 18. 20. A personal computer which uses the heat release sheet as recited in claim 19 of the patent application. 21. A game machine that uses a heat release sheet as recited in claim 19, item -9 - (6) (6) 1328018. 22. A digital camera </ RTI> which uses a heat release sheet as recited in claim 19 of the patent application. A digital camera which uses the heat release sheet as described in claim 19 of the patent application. 24. A television characterized by the use of a heat release sheet as recited in claim 19 of the scope of the patent application. A portable telephone characterized by using a heat release sheet as described in claim 19 of the patent application. 26. The method for producing a composite material according to claim 13, wherein the carbon material and the ceramic are stirred by dry shearing, and the obtained composition is dispersed in a polymer material or an oil. 27. The method for producing a composite material according to claim 14, wherein the gas phase carbon fiber and the ceramic particle having an aspect ratio of 5 to 1 Å have an adhesive property with respect to an average fiber diameter of 10 to 500 nm. The polymer compound is a composite of the vapor-phase carbon fiber on the surface of the ceramic particles, and the obtained composition is dispersed in a polymer material or an oil composition of the composite material of the present invention, and contains a ceramic having a functional group on the surface thereof. Ceramics contain a lightweight and highly thermally conductive carbon material. Compared with the case where only the same amount of ceramic is used as the chelating agent, the amount of addition of the composite material to the same thermal conductivity can be small. Lightweight. On the one hand, 'will be used as a squeezing agent to knead only the same amount of carbon material, because it contains ceramics with functional groups on the surface, so it can be filled more 'to make the composite material a higher thermal conductivity》 -10 · (7) (7) 1328018 In addition, as the added ceramic, it is possible to select a small density, and it is possible to maintain a certain thermal conductivity and to be lighter. In the added carbon material, a person having a high heat conductivity can be selected, and a certain quality can be maintained while a higher thermal conductivity can be achieved. Such a composition, a polymer material or an oil, is a composite material of the invention, which is not achievable in a conventional composite material, but is lightweight and has high heat conductivity. Then, the molded article of the present invention obtained by molding the composite material is also lightweight and has high thermal conductivity, and since it has excellent heat dissipation properties, it can be suitably used in recent years due to high performance of electronic devices or electric parts. A heat release sheet or a heat release film which is a problem in which the temperature rise due to heat generation of the LSI is suppressed. BEST MODE FOR CARRYING OUT THE INVENTION The composition for a composite material of the present invention contains a carbon material and a ceramic. For the carbon material, carbon fiber (thermal conductivity: 400 to 1200 w/(mk)), carbon nanotube (thermal conductivity: 400 to 1200 w/(m · k )), pitch or pan-based carbon fiber (for thermal conductivity: 400 to 1200 w/(mk)) can be used. Carbon fiber such as thermal conductivity 200~ lOOOw/(m, k)), coke powder (thermal conductivity 1〇〇~200w/(m · k )), graphite powder (thermal conductivity 100 〜200w/(mk)) At least one of them. Among these, carbon fibers having excellent thermal conductivity are preferred, and gas phase carbon fibers or carbon nanotubes having higher thermal conductivity are preferred. In addition, when it is a material that can be uniformly dispersed in a polymer material or an oil, a gas-phase carbon fiber having a small specific surface area is preferable (gas phase carbon fiber-11 - (8) 1328018 The specific surface area is 1 〇 20 20 m 2 /g, and the specific surface area of the carbon nanotubes is 200 〜 * 3 00 m 2 /g ). In the case of using a carbonaceous carbon fiber, the average fiber diameter is preferably 50 to 500 nm, more preferably 70 to 3 nm, still more preferably 80 to 200 nm, and particularly preferably 100 to I50 nm. When the average fiber diameter is less than 50 nm, the handleability is lowered, and when the average fiber diameter exceeds 50 Å, the aspect ratio becomes small to lower the thermal conductivity. The aspect ratio of the φ gas phase carbon fiber is preferably from 5 to 1,000, more preferably from 10 to 500, still more preferably from 15 to 150, and particularly preferably from 20 to 120. When the aspect ratio is 5 or more, the thermal conductivity is improved, and when the aspect ratio is 1 000 or less, the treatment is good. Further, by making the aspect ratio of the vapor-phase carbon fiber to be used 5 or more and less than 40, the fluidity of the composition for a composite material in the composite material can be improved, and the gas phase carbon fiber having an aspect ratio of 40 or more can be added. In contrast, the thermal conductivity is not reduced and its viscosity is in a smaller range. Φ Specifically, the ceramics of the present invention using aluminum oxide has a thermal conductivity of 1.6 (W/(mK)) or more and a viscosity of 丨 (^ jaws is 2 〇 • (Pa.s) or less, in l 〇〇 rpm is less than 30 (Pa.s). In addition, the case of using boron nitride in ceramics is '2.0 (W/ ( m · κ )) or more, and more preferably 2.5 (W/(m*K). Further, it is preferably 2.8 (W/(mK)) or more, and the viscosity thereof is 30 (Pa · s ) or less at 10 rpm, and 40 (Pa.s) or less at 100 rpm. It is from 1 to 39, and further preferably from 15 to 38, particularly preferably from 20 to 38. -12- (9) (9) 1328018 All of the above carbon materials can be used in the market. Various known documents exist, and β can be produced in accordance with the above. In the case of a gas phase carbon fiber, an organic compound such as benzene which is a raw material is used together with an organic transition metal compound such as ferrocene as a catalyst. The carrier gas is introduced into a high-temperature reaction furnace and can be produced by gas phase thermal decomposition. For example, a method for producing thermally decomposed carbon fibers on a substrate is disclosed (JP-A-60-27700) In the method of producing a thermally decomposing carbon fiber in a floating state (Japanese Unexamined Patent Application Publication No. Hei No. Hei No. 60-5499 No. 8), a method of growing a thermally decomposable carbon fiber in a reactor wall (Japanese Patent No. 2778434), etc., is used in the present invention. The carbon fiber can be produced by such a method. The vapor-processed carbon fiber produced in this manner can be used as a raw material as it is, but in the state of the gas phase growth, there is a thermal decomposition product or an adhesion of an organic compound or the like from the raw material. The crystal structure of the carbon fiber-forming fiber structure is insufficient. Therefore, in order to remove the impurities such as the thermal decomposition product and improve the crystal structure as the carbon fiber, the heat treatment can be performed in an inert gas atmosphere. In the inert gas such as argon, heat treatment at about 800 to 15 00 ° C is preferably carried out in an inert gas such as argon. Further, in order to improve the crystallinity of the carbon structure, it is carried out in an inert gas such as argon for about 2000 〜 The heat treatment at 3 000 ° C is preferred. The gas phase carbon fiber treated in this manner is, for example, VGCF (registered trademark: manufactured by Showa Denko Co., Ltd.). It is sold in the market. The carbon material is a carbon nanotube tube. The average fiber diameter is preferably 3 to 50 nm, more preferably 3 to 40 nm, and further preferably 3 to 30 nm. Special-13 - (10) (10) 1328018 is preferably 3 to 20 nm. The fiber length is preferably 2 to 20 μm, more preferably 5 to 15 μm, and further preferably 6 to 13 μm, particularly preferably 8 to 12 μm. The carbon nanotube used in the present invention can be used. Generally, the products that are commercially available, as well as the records of most existing documents, are easily synthesized if they are familiar with the art. The ceramic used in the present invention is uniformly dispersed in a polymer material or an oil which is a matrix material. It is preferably at least one selected from the group consisting of alumina, magnesia, cerium nitride, boron nitride, and aluminum nitride. Among them, boron nitride, aluminum oxide and/or magnesium oxide are more preferable because they have a good affinity with a high molecular material or an oil, and are easily formed by air bubbles during molding. The thermal expansion rate is 1xl〇_0/°C for boron nitride, 6xl for alumina (T6/°C, and 14x1 for magnesium oxide (T6/°C, boron nitride and alumina are compared with other enthalpy due to heat) The amount of change in volume is small, and the peeling at the interface with the polymer material or the oil can be reduced. Therefore, the ceramic used in the present invention is particularly preferably alumina. The ceramic used in the present invention has particles having an average particle diameter of 0.3 to 80 μm. Preferably, it is preferably 0.5 to 70 μm, and when the average particle diameter is 0·3 μm or more, the handleability is good, and when the average particle diameter is 80 μm or less, the strength is not lowered, and the planar smoothness can be maintained. The specific surface area measured by the nitrogen adsorption method (BET method) is preferably 〇_〇1 to 15 m2/g, preferably 0.01 to 10 m2/g. Further, when the specific surface area is 0.01 m2/g or more, the decrease in strength can be suppressed, and the specific surface area is When the amount is less than 15 m2/g, the amount of ceramics to be reduced can be suppressed. In the composition of the present invention, the amount of the carbon material is preferably 0.1 to 20% by mass based on the amount of the ceramic compound, and more preferably 5% to 10% by mass. %' is particularly preferably 0.8 to 8 mass%. The amount of carbon material is the mass. In the case of the above, when the heat transfer effect is obtained and the amount is 20% by mass or less, the handleability is good. -14 - (11) 1328018 The method of mixing the carbon material and the ceramic is not particularly limited, but the carbon material is carbon fiber, especially In the case of using a gas phase carbon fiber, it is preferable to use a Henschel honing machine, a ball mill or a jet honing machine to apply a shearing force for a short period of time. It is preferable to mix by applying a shearing force to have a three-dimensional element. The whole or a part of the vapor-phase carbon fiber of the three-dimensional structure is unwound, and it is highly dispersible when mixed with a polymer material or an oil. The polymer compound used in the present invention is a gas phase carbon fiber and a φ ceramic. a polymer having a binding property, wherein the polymer compound having a bonding property is such that the ceramic and the gas phase carbon fiber are brought into contact with each other so as to be covalently bonded between the two objects. Chemical bonding of van der Waals, hydrogen bonds, etc. becomes the state in which the two objects are integrated. In the mixing, stirring, solvent removal, heat treatment, etc., the carbon fiber of the vapor phase method is peeled off. The degree of non-occurrence is not applicable to the force of compression, bending, peeling, impact, stretching, tearing, etc., and it can be applied as a polymer compound having a viscosity of ♦. &gt; The polymer compound may be at least one selected from the group consisting of a phenol resin, a polyvinyl alcohol resin, a furan resin, a cellulose resin, a polystyrene resin, a polyfluorene imide resin, and an epoxy resin. Phenol tree.. Lipid, polyvinyl alcohol' is preferably a phenol resin. In particular, a composite material in which a dense dry oil or a fatty acid phenol resin is used can obtain a more dense adhesive property. This is a 'phenol resin and dryness. The unsaturated bond in the oil produces a chemical reaction, which becomes a so-called dry oil-modified phenol resin, and it is presumed that it is decomposed during the hardening process to prevent foaming. Moreover, the dry oil is not only a double bond* but a relatively long alkyl and ester bond, which is -15- (12) (12)

1328018 認爲在硬化過程中在氣體之易於排出等方面並 苯酚樹脂係由苯酚類及醛類之反應而製tt 醛清漆，可溶酚醛樹脂等之未改性苯酚樹脂骂 之苯酚樹脂。又，可因應需要將腈橡膠等之精 酚樹脂使用。例如苯酚類方面，可例舉苯酚、 苯酚，具有C20以下烷基之烷基苯酚。在將氧 肪酸混合之苯酚樹脂，係預先使苯酚類與乾招 媒存在下進行加成反應，其後添加鹼性觸媒恒 行甲醛加成反應者，或使苯‘酚類及甲醛反應， 性油亦可。 乾性油係通常所知之桐油、亞麻仁油、肢 大豆油、檟如堅果油等，該等可爲其脂肪酸， 在空氣中放置時具有可在比較短的時間進行固 質的植物油。相對於苯酚樹脂之乾性油或其脂 ，例如相對於（苯酚及甲醛之縮合物）100 % 乾性油或其脂肪酸）5〜50質量份爲適當。若 更多時，黏接性降低氣相法碳纖維之密度也降 質量份更少時則無法獲得緻密複合材料。 使用此高分子化合物在陶瓷使氣相法碳纖 形，使高分子化合物以丙酮，乙醇，或甲苯等 黏度時則易於黏接。 高分子化合物在陶瓷外表面之至少一部份 論全面爲均一，不均一而實質上黏接者爲佳。 氛圍方面，可爲大氣壓下（常壓下），加壓下 無相關。 i，可使用酚 之一部份改性 I膠混合於苯 甲酚、二甲 乞性油或其脂 Ξ油在強酸觸 ί系呈鹼性進 其後添加乾 ί水蓖麻油、 係成爲薄膜 丨化乾燥之性 丨肪酸之比率 :量份，以（ 比50質量份 :低。若比 5 丨維黏接之情 I稀釋來調整 '，較佳爲不 在黏接時之 ，減壓下之 -16 - (13) 1328018 任一情形，在減壓下黏接之情形，以可提高與陶瓷，氣相 * 法碳纖維及高分子化合物之親和性故爲佳。 ' 在陶瓷，氣相法碳纖維及高分子化合物之混合，攪拌 方法方面，並無特別限定，但，可使用例如螺旋帶式混合 機（ribbon mixer)、螺旋型捏合機、spartan顆粒機' Ladyge混合機、行星混合機、萬能混合機等之裝置。 攪拌處理時之溫度及時間，可因應陶瓷，氣相法碳纖 φ 維及高分子化合物之成分及黏度等而適宜選擇，而通常以 〇〜50 °C左右，較佳爲10〜3 0°C左右之範圍。或混合物之 黏度在混合溫度下成爲5 OOPa · s以下之方式進行混合時間 及組成物之溶劑稀釋。在此情形，溶劑方面可使用與陶瓷 ，氣相法碳纖維及高分子化合物之親和性良好之物，而可 例舉醇類 '酮類 '芳香族烴及酯類。較佳爲甲醇、乙醇、 丁醇、丙酮、甲基乙基酮、甲苯、乙酸乙酯、乙酸丁酯等 〇 • 攪拌後，以可除去溶劑之一部份或者全部爲佳。除去 方法可使用熱風乾燥，真空乾燥等周知之方法。乾燥溫度 .係依使用之溶劑之沸點，蒸氣壓等而定，具體言之爲5 0 °C 以上，較佳爲100〜1000。(：，進而較佳爲150〜500 ec。 在加熱硬化可使用周知之加熱裝置。但是，在製造步 驟方面就連續處理爲可行之旋轉窯（rotary kiln)或帶式 連續爐等在生產性之點而言爲佳。 相對於陶瓷及氣相法碳纖維總量之高分子化合物之添 加量，在例如苯酚樹脂時，較佳爲0 · 1質量％〜3 0質量％ -17- (14) 1328018 ’進而較佳爲Ο·1〜20質量％，特佳爲〇1〜15質量9? 添加0.1質量％以上’可使陶瓷表面以聚合物覆蓋， 爲3 0質量％以下’可抑制粒子彼此之間之接觸電阻。 進而’將陶瓷及氣相法碳纖維藉由黏合劑予以複 ’而可提高粒子彼此之間之滑動性（slidable )，造 充塡於基質之際流動性惡化之最重要原因，粒子之接 阻之減低爲可行’與習知比較可獲得高度流動性。 φ 在使用本發明之複合材料用組成物下，可獲得高 性且高流動性之複合材料。本發明之複合材料，其導 與該等使用於在陶瓷表面具有黏接性之高分子化合物 附著氣相法碳纖維之情形比較，其比率並非在80%以 且黏度在lOrpm爲25(Pa.s)以下，在l〇〇rpm爲 Pa · s )以下，較佳爲在i00rpm爲1〇 ( Pa . s )以下 而較佳爲5 (Pa. s)以下。 本發明之複合材料係將該組成物良好的分散於高 φ 材料或油類中。 高分子材料或油類方面，可使用周知之物，較佳 , 子材料方面’有例如脂肪族系樹脂、不飽和聚酯樹脂 • 烧酸樹脂、甲基丙烯酸樹脂、乙烯酯樹脂、環氧樹脂 砂氧樹脂等，較佳油類方面，有例如聚矽氧油、石油 '氟系油等。該等通常可單獨使用，亦可將二種以上 。該等中’環氧樹脂、聚矽氧樹脂可進行薄膜之塗佈 在樹脂中導熱性優異爲佳。 碳材·料’更佳爲氣相法碳纖維或者碳奈米管，進 ，。在 在成 合化 成高 觸電 導熱 熱率 而不 下， 20 ( ，進 分子 高分 、丙 、聚 系油 倂用 ，因 而較 -18- (15) (15)1328018 佳爲含有氣相法碳纖維之本發明複合材料之導熱率，相對 於不含碳材料之複合材料，亦即相對於僅添加陶瓷所成複 合材料之導熱率，其比率爲1_0以上。亦即，本發明之複 合材料’其導熱率相對於對陶瓷比之導熱率爲1.0以上之 複合材料。 在後述實施例1 ’ 2，4，6 ’ 7，8及比較例1之實驗 結果方面’在橫軸相對於陶瓷配合量（X)與氣相法碳纖 維配合量（Y)之合計之氣相法碳纖維配合量（γ)之比 ’亦即氣相法碳纖維取代比·率（％ )，縱軸則繪出對陶瓷 導熱率之圖形如第1圖所示。 本發明之複合材料中高分子材料或油類之配合量，以 碳材料及陶瓷合計量之1〜35質量％爲佳，進而較佳爲1 〜2 5質量％。 配合量爲1質量％以上時流動性爲良好，35質量％以 下時可賦予高導熱性。 在將該組成物分散於高分子材料或油類中之方法並無 特別限定。在碳材料係使用碳纖維之情形，碳纖維係纖維 徑細纖維彼此之間易於集中，故在配合於高分子材料或油 類之前以使用Henschel硏磨機等之攪拌機以乾式混合攪 拌爲佳。相對於已混合攪拌之組成物添加高分子材料或油 類，施以和緩之剪斷力，在高分子材料或油類中可良好地 分散。 在分散處理後，藉由離心脫泡機來進行脫泡處理可賦 予穩定地且高的導熱率。進而關於添加之碳材料，係如氣 -19- (16) (16)1328018 相法碳纖維般藉由剪斷應力將纖維折彎，有導熱率降低之 可能性，故捏合時之旋轉速度以50rpm以下爲佳。 本發明之成形體係輯由上述複合材料之成形加工而得 。成形方法方面，可使用FRP成形’轉送成形等之壓縮成 形法 '鑄模成形' 封入鑄型等之鑄型法、壓延（calender )成形等之輥加工法、RIM成形、射出發泡成形等之射出 成形法 '擠壓發泡成形等之發泡技術法、膨脹（inflation )薄膜成形、T模薄膜成形等之擠壓成形法等可依照目的 需要使用成形法。而爲獲得·薄片狀或者薄膜狀之成形體， 以輥加工法及擠壓成形法爲佳。 依照本發明所得成形體，輕量化與高導熱性可均衡性 良好的，高等級達成，可作爲電子裝置、電子零件等之放 熱構件使用。尤以，可成形爲薄片狀或薄膜狀之成形體， 因放熱性優異，故近年來爲電子裝置高性能化之而成爲問 題之LSI之發熱所致溫度上昇可予抑制之放熱薄片來使用 〇 用於本發明之放熱薄片之電子裝置或電子零件，可使 用於例如個人電腦、遊戲機、數位攝影機、數位相機、電 視、攜帶電話等。尤以放熱性能優異，故可搭載於小型電 子製品。 【實施方式】 實施發明之最佳型態 以下，依據實施例及比較例，具體說明本發明，但本 -20- (17) 1328018 發明並非限定於該等之例。 此外’在各例中，成形體試料之導熱率及 下方法予以測定。 •導熱率： 使用迅速熱電率測定計（QTM-500型，京 製）’根據試料非定常細線加熱法（熱線法） 內使試料保持於23°C之溫度後進行測定。 •黏度： B型黏度計（BROOKFIELD工程公司製） 轉速度個別之 lOrpm及 lOOrpm來測定攪拌1 〇 又，實施例15〜17及比較例7〜8中使用 以其次之方法製造。 將桐油100質量份與苯酚150質量份，壬 質量份混合並保持於50°C。對此添加0.5質量 攪拌，予以緩緩地昇溫在120°C保持1小時， 苯酚類之加成反應。其後使溫度降至6 0 °C以下 基四胺6質量份及37質量％»甲醛100質量份 行約2小時反應，其後予以真空脫水後，添加 量份，丙酮100質量份予以稀釋，獲得黏度 20°C )之清漆（稱爲清漆A)。 實施例1: 將平均粒徑39μπι，BET比表面積〇.5m2/g 黏度係由以 都電子工業 ’在恒溫室 ，就轉子旋 分後之黏度 之清漆A可 基苯酚15〇 份之硫予以 進行桐油與 ，添加亞S ，在90°C進 甲醇100質 2 0 m P a · s ( 之氧化鋁（ -21 - (18) (18)1328018 AS10’昭和電工公司製）396g，與平均纖維徑I50nm，長 寬比70之氣相法碳纖維（VGCF，昭和電工公司製）4g以 Henschel硏磨機混合1〇秒。將含有所得之氧化鋁及氣相 法碳纖維之組成物，充塡於市售之二液型聚矽氧油（ TSE3070’ GE東芝聚矽氧公司製）10〇g，以捏合機（τκ HI VIS MIX®，特殊機化工業公司製），使旋轉速爲5 〇rpm 經1 〇分鐘捏合。其後，以離心脫泡機，使旋轉速度爲 45〇rpm經5分鐘處理裝塡於型箱（shoe)後，以真空乾燥 機使溫度爲1 2 〇 °C經2小時靜置予以硬化獲得橡膠狀之成 形體。 將所得之成形體切割成寬100mm，深度50mm，高 2 0mm來測定導熱率。 實施例2 : 將平均粒徑39μιη，BET比表面積0.5m2/g之氧化鋁（ AS10’ 0召和電工公司製）380g，與平均纖維徑150nm，長 寬比7〇之氣相法碳纖維（VGCF，昭和電工公司製）20g 以Henschel硏磨機混合1〇秒。將含有所得之氧化鋁及氣 相法碳纖維之組成物，充塡於市售之聚矽氧油（TSE3070 ，GE東芝聚矽氧公司製）100g，以捏合機（T.K. HIVIS MIX®，特殊機化工業公司製），使旋轉速爲5 Orpin經10 分鐘捏合。其後，以離心脫泡機使旋轉速度成爲45〇rpm 經5分鐘處理裝塡於型箱後，以真空乾燥機，使溫度爲 1 20 °C靜置2小時使之硬化獲得橡膠狀之成形體。所得之 -22- (19) (19)1328018 成形體切割成寬100mm，深度50mm’高20mm來測定導 熱率。 實施例3 : 將平均粒徑39μπι，BET比表面積〇.5m2/g之氧化鋁（ AS10，昭和電工公司製）594g，與平均纖維徑150nm，長 寬比70之氣相法碳纖維（VGCF，昭和電工公司製）6g以 Henschel硏磨機混合1〇秒。將含有所得之氧化錯及氣相 法碳纖維之組成物充塡於市·售之聚矽氧油（TSE 3070，GE 東芝聚矽氧公司製）100g，以捏合機（Τ·Κ· HIVIS MIX® ，特殊機化工業公司製），使旋轉速爲5 Orpm經10分鐘 捏合。其後，以離心脫泡機，使旋轉速度成爲45 Orpm經 5分鐘處理裝塡於型箱後，以真空乾燥機，使溫度爲 1 20°C靜置2小時使之硬化獲得橡膠狀之成形體。所得之 成形體切割成寬100mm，深度50mm，高20mm來測定導 熱率. 實施例4 : 將平均粒徑39μιη，BET比表面積〇.5m2/g之氧化鋁（ AS10，昭和電工公司製）3 80 g，與平均纖維徑150nm， 長寬比30之氣相法碳纖維（VGCF-H，昭和電工公司製） 20g以Henschel硏磨機混合10秒。將所得之含有氧化鋁 及氣相法碳纖維之組成物，充塡於市售之聚矽氧油（ TSE3 07 0，GE東芝聚矽氧公司製）100g，以捏合機（τ.Κ· -23- (20) (20)1328018 HI VIS MIX® ’特殊機化工業公司製）使旋轉速爲50rpm 經1 〇分鐘捏合。其後，以離心脫泡機，使旋轉速度成爲 4 5 Orpm ’經5分鐘處理裝塡於型箱後，以真空乾燥機，使 溫度爲1 2〇°C靜置2小時使之硬化獲得橡膠狀之成形體。 所得之成形體切割成寬100mm，深度 50mm，高 20mm來測定導熱率。 實施例5 : 將平均粒徑39μπι，BET比表面積0.5m2/g之氧化鋁（ AS10，昭和電工公司製）5 8 8g，與平均纖維徑150nm，長 寬比 30之氣相法碳纖維（VGCF-H，昭和電工公司製） 12g以Hensche】硏磨機混合1〇秒。將所得之含有氧化鋁 及氣相法碳纖維之組成物，充塡於市售之聚矽氧油（ TSE3070，GE東芝聚矽氧公司製）l〇〇g，以捏合機（τ.Κ. HIVIS MIX®，特殊機化工業公司製），使旋轉速爲50rpm ，經1 〇分鐘捏合。其後，以離心脫泡機，使旋轉速度成 爲450rpm經5分鐘處理裝塡於型箱後，以真空乾燥機， 使溫度爲120°C靜置2小時使之硬化獲得橡膠狀之成形體 〇 所得之成形體切割成寬100mm，深度50mm，高 2 0 m m來測定導熱率。 實施例6: 將平均粒徑39μιη ’ BET比表面積〇.5m2/g之氧化鋁（1328018 It is considered that a phenol resin is a phenol resin which is a non-modified phenol resin such as a phenol resin or a phenol resin by a reaction of phenols and aldehydes in the process of easy gas discharge during hardening. Further, a phenol resin such as a nitrile rubber can be used as needed. Examples of the phenols include phenol and phenol, and alkylphenols having an alkyl group having a C20 or lower. The phenol resin in which the fatty acid is mixed is subjected to an addition reaction in the presence of a phenol and a dry medium, and then a basic catalyst is added to the formaldehyde addition reaction, or the benzene 'phenol and formaldehyde are reacted. , oil can also be. Dry oils are commonly known as tung oil, linseed oil, limb soybean oil, such as nut oil, etc., which are fatty acids which, when placed in air, have vegetable oils which can be solidified in a relatively short period of time. The dry oil of the phenol resin or the fat thereof is, for example, 5 to 50 parts by mass based on 100% of the dry oil (a condensate of phenol and formaldehyde) or a fatty acid thereof. If more, the adhesion is lower and the density of the fumed carbon fiber is also reduced. When the mass fraction is less, the dense composite material cannot be obtained. The polymer compound is used to form a vapor phase carbon in a ceramic, and the polymer compound is easily adhered when it is made of acetone, ethanol, or toluene. The polymer compound is uniform in at least part of the outer surface of the ceramic, and is not uniform and is substantially bonded. In terms of atmosphere, it can be under atmospheric pressure (under normal pressure) and there is no correlation under pressure. i, one part of the modified phenol can be mixed with cresol, dimethyl hydrazine or its fat eucalyptus oil. After the strong acid touches the alkali, it is added with dry eucalyptus oil and becomes a film. The ratio of deuterated dry fatty acid: the amount, in parts (50 parts by mass: low. If it is adjusted by the dilution of 5 丨 黏 I, it is better not to be bonded, under reduced pressure) -16 - (13) 1328018 In any case, it is preferable to bond under reduced pressure to improve the affinity with ceramic, gas-phase carbon fiber and polymer compounds. 'In ceramics, gas phase method The mixing of the carbon fiber and the polymer compound, and the stirring method, are not particularly limited, but for example, a ribbon mixer, a spiral kneader, a spartan pellet machine 'Ladyge mixer, a planetary mixer, a universal one can be used. A device such as a mixer, etc. The temperature and time during the agitation treatment may be appropriately selected depending on the ceramic, the gas phase carbon fiber φ and the composition and viscosity of the polymer compound, and are usually about 5050 ° C, preferably 10~3 0 °C or a mixture of mixtures The mixing time and the solvent dilution of the composition are carried out at a mixing temperature of 5 ÅPa·s or less. In this case, a solvent having good affinity with ceramics, vapor-phase carbon fibers, and a polymer compound can be used. An alcoholic 'ketone' aromatic hydrocarbon and an ester may, for example, be preferably methanol, ethanol, butanol, acetone, methyl ethyl ketone, toluene, ethyl acetate or butyl acetate. A part or all of the solvent may be removed. The removal method may be a method known as hot air drying, vacuum drying, etc. The drying temperature depends on the boiling point of the solvent used, the vapor pressure, etc., specifically 50 °. C or more, preferably 100 to 1000. (:, further preferably 150 to 500 ec. A well-known heating device can be used for heat curing. However, continuous processing is a feasible rotary kiln in terms of a manufacturing step. Or a belt-type continuous furnace is preferable in terms of productivity. The amount of the polymer compound added to the total amount of the ceramic and vapor-phase carbon fibers is preferably from 0.1 to 3% by mass in the case of, for example, a phenol resin. 0 Mass % -17- (14) 1328018 ' Further preferably Ο·1~20% by mass, particularly preferably 〇1~15 mass 9? Adding 0.1% by mass or more 'can make the ceramic surface covered with polymer, is 3 0 The mass % or less 'can suppress the contact resistance between the particles. Further, 'the ceramic and the vapor-phase carbon fiber are complexed by the binder' to improve the slidability of the particles and to build up the matrix. The most important reason for the deterioration of the fluidity is that the reduction of the resistance of the particles is feasible. A high degree of fluidity can be obtained by comparison with the conventional ones. φ High and high fluidity can be obtained by using the composition for a composite material of the present invention. Composite material. The composite material of the present invention is compared with the case where the polymer compound having adhesion to the ceramic surface is attached to the vapor phase carbon fiber, the ratio is not 80% and the viscosity is 25 at 10 rpm (Pa.s). The following is preferably 1⁄2 (Pa.s) or less, and preferably 5 (Pa.s) or less at 100 rpm, preferably at 100 rpm. The composite material of the present invention is a good dispersion of the composition in a high φ material or oil. As the polymer material or the oil, a well-known thing can be used, and preferably, the sub-materials are, for example, an aliphatic resin, an unsaturated polyester resin, a sulphuric acid resin, a methacrylic resin, a vinyl ester resin, or an epoxy resin. As the sand oxide resin or the like, preferred oils include, for example, polyoxyphthalic acid oil and petroleum 'fluorine-based oil. These may be used alone or in combination of two or more. These 'epoxy resins and polyoxyxylene resins can be applied to a film. It is preferred that the resin has excellent thermal conductivity. The carbon material/material is more preferably a gas phase carbon fiber or a carbon nanotube tube. In the formation of high electric shock heat transfer rate, 20 (, into the molecular high score, C, poly oil use, and thus -18- (15) (15) 1328018 better than the gas phase carbon fiber of the present invention The thermal conductivity of the composite material is relative to the thermal conductivity of the composite material containing no carbon material, that is, the composite material formed by adding only ceramics, and the ratio thereof is 1_0 or more. That is, the composite material of the present invention has a relatively high thermal conductivity. A composite material having a thermal conductivity of 1.0 or more for ceramics. In the experimental results of Examples 1 '2, 4, 6' 7, 8, and Comparative Example 1 described later, 'the amount of the horizontal axis relative to the ceramic compound (X) and The ratio of the gas phase method carbon fiber compounding amount (Y) to the gas phase method carbon fiber compounding amount (γ) is also the gas phase carbon fiber substitution ratio (%), and the vertical axis is a graph showing the thermal conductivity of the ceramic. In the composite material of the present invention, the amount of the polymer material or the oil is preferably from 1 to 35 mass%, more preferably from 1 to 25 mass%, based on the total amount of the carbon material and the ceramic. When the mass is 1% by mass or more, the fluidity is good, 35 The method of dispersing the composition in a polymer material or an oil is not particularly limited. When the carbon material is a carbon fiber, the carbon fiber-based fiber diameter fiber is easy to be used. Concentration, it is preferable to use a mixer such as a Henschel honing machine to dry mix and stir before blending with a polymer material or oil. Add a polymer material or oil to the composition to be mixed and stirred, and apply a gentle shear. The breaking force is well dispersed in the polymer material or the oil. After the dispersion treatment, the defoaming treatment by the centrifugal defoaming machine can impart a stable and high thermal conductivity. Further, regarding the added carbon material, If the gas is bent by the shear stress, the thermal conductivity is reduced, so the rotation speed at the time of kneading is preferably 50 rpm or less. The system is obtained by molding the above-mentioned composite material, and a molding method such as a compression molding method such as transfer molding, which is formed by FRP molding, and a mold-molding method, such as a mold, can be used. Rolling method such as calender molding, injection molding method such as RIM molding and injection foam molding, foaming technique such as extrusion foam molding, expansion film formation, and T-die film molding The press molding method and the like may be carried out according to the purpose, and it is preferable to obtain a sheet-like or film-like molded body by a roll processing method or an extrusion molding method. The molded article obtained according to the present invention has a lightweight and high thermal conductivity. It can be used as a heat releasing member such as an electronic device or an electronic component, and can be used as a heat releasing member such as an electronic device or an electronic component. In particular, it can be molded into a sheet-like or film-shaped molded body, and is excellent in heat dissipation, so that it is high in electronic devices in recent years. An electronic device or an electronic component used for the heat release sheet of the present invention can be used for, for example, a personal computer, a game machine, a digital camera, or the like, which can be used as a heat release sheet which can be suppressed by the heat generation of the LSI which is a problem. Digital camera, TV, mobile phone, etc. In particular, it is excellent in heat release performance and can be mounted on small electronic products. [Embodiment] BEST MODE FOR CARRYING OUT THE INVENTION Hereinafter, the present invention will be specifically described based on examples and comparative examples, but the invention is not limited to the examples. Further, in each of the examples, the thermal conductivity of the molded article sample and the following method were measured. • Thermal conductivity: A rapid pyroelectricity meter (QTM-500 type, manufactured by Kyoyo Co., Ltd.) was used. The sample was kept at a temperature of 23 ° C according to the sample unsteady thin wire heating method (hot wire method). • Viscosity: B-type viscometer (manufactured by BROOKFIELD Co., Ltd.) The rotation speed was measured by lOrpm and lOOrpm, respectively, and the stirring was performed for 1 〇. Further, in Examples 15 to 17 and Comparative Examples 7 to 8, the second method was used. 100 parts by mass of tung oil and 150 parts by mass of phenol and 壬 parts by mass were mixed and kept at 50 °C. To this, 0.5 mass of agitation was added, and the temperature was gradually raised to 120 ° C for 1 hour to carry out an addition reaction of phenols. Thereafter, the temperature is lowered to 6 0 ° C below 6 parts by mass of the tetraamine and 37% by mass of the formaldehyde to 100 parts by mass for about 2 hours, followed by vacuum dehydration, and the amount of the mixture is diluted with 100 parts by mass of acetone. A varnish (referred to as varnish A) having a viscosity of 20 ° C was obtained. Example 1: The average particle diameter of 39 μm and the BET specific surface area of 55 m 2 /g were carried out by the sulphur of the varnish A-based phenol of the viscosity of the rotor in the thermoelectric chamber in the thermostatic chamber. Tung oil and, add sub-S, enter methanol at 90 °C, 100 masses of 20 m P a · s (alumina (-21 - (18) (18) 1328018 AS10 'Showa Denko) 396 g, with average fiber diameter 4 g of a gas-phase carbon fiber (VGCF, manufactured by Showa Denko Co., Ltd.) having an aspect ratio of 70 and an aspect ratio of 70 g were mixed in a Henschel honing machine for 1 sec. The composition containing the obtained alumina and fumed carbon fiber was filled with a commercially available product. The second liquid type polyoxyxide oil (TSE3070' GE Toshiba Polyoxo Co., Ltd.) 10〇g, which is a kneading machine (τκ HI VIS MIX®, manufactured by Special Machine Chemical Co., Ltd.), and the rotation speed is 5 rpm. After kneading in a minute, the centrifugal defoaming machine was placed at a rotation speed of 45 rpm for 5 minutes to be mounted on a shoe, and then dried at a temperature of 1 2 〇 ° C for 2 hours in a vacuum dryer. It is set to be hardened to obtain a rubber-like formed body. The obtained formed body is cut into a width of 100 mm and a depth of 50 mm. The thermal conductivity was measured at a height of 20 mm. Example 2: 380 g of alumina having an average particle diameter of 39 μm and a BET specific surface area of 0.5 m 2 /g (manufactured by AS 10'Okatowa Electric Co., Ltd.), and an average fiber diameter of 150 nm, aspect ratio 7 20 g of gas-phase carbon fiber (VGCF, manufactured by Showa Denko Co., Ltd.) was mixed with a Henschel honing machine for 1 sec. The composition containing the obtained alumina and fumed carbon fiber was charged to a commercially available polyfluorene oxide oil. (TSE3070, manufactured by GE Toshiba Polyoxo Co., Ltd.) 100 g, kneaded by a kneading machine (TK HIVIS MIX®, manufactured by Kekyo Kogyo Co., Ltd.) at a rotation speed of 5 Orpin for 10 minutes. Thereafter, a centrifugal defoamer was used. The rotation speed was changed to 45 rpm. After being placed in a mold for 5 minutes, the mixture was allowed to stand at a temperature of 1 20 ° C for 2 hours to obtain a rubber-like molded body by a vacuum dryer. The obtained -22- (19) (19) 1328018 The molded body was cut into a width of 100 mm and a depth of 50 mm' and a height of 20 mm to measure the thermal conductivity. Example 3: Alumina having an average particle diameter of 39 μm and a BET specific surface area of 55 m 2 /g (AS10, manufactured by Showa Denko Corporation) 594g, with a mean fiber diameter of 150nm, an aspect ratio of 70 gas phase method 6 g of carbon fiber (VGCF, manufactured by Showa Denko Co., Ltd.) was mixed in a Henschel honing machine for 1 sec. The composition containing the obtained oxidized and gas-phase carbon fiber was filled with a commercially available polyoxyxene oil (TSE 3070, GE). 100 g of Toshiba Polyoxane Co., Ltd. was kneaded by a kneading machine (Τ·Κ·HIVIS MIX®, manufactured by Kekyo Kogyo Co., Ltd.) at a rotation speed of 5 O rpm for 10 minutes. Thereafter, the centrifugal defoaming machine was used, and the rotation speed was changed to 45 O rpm for 5 minutes to be mounted on the mold, and the mixture was allowed to stand at a temperature of 1 20 ° C for 2 hours to obtain a rubber-like shape by a vacuum dryer. body. The obtained molded body was cut into a width of 100 mm, a depth of 50 mm, and a height of 20 mm to measure the thermal conductivity. Example 4: Alumina (AS10, manufactured by Showa Denko KK) having an average particle diameter of 39 μm and a BET specific surface area of 55 m 2 /g g, 20 g of a vapor-phase carbon fiber (VGCF-H, manufactured by Showa Denko Co., Ltd.) having an average fiber diameter of 150 nm and an aspect ratio of 30 was mixed in a Henschel honing machine for 10 seconds. The obtained composition containing alumina and fumed carbon fiber was charged with 100 g of a commercially available polyoxyxylene oil (TSE3 07 0, manufactured by GE Toshiba Polyoxo Co., Ltd.) as a kneading machine (τ.Κ·-23 - (20) (20) 1328018 HI VIS MIX® 'Made in Kogyo Co., Ltd.' was kneaded at a rotation speed of 50 rpm for 1 minute. Thereafter, the centrifugal defoaming machine was used, and the rotation speed was changed to 4 5 Orpm. After being treated in a mold box for 5 minutes, the mixture was allowed to stand at a temperature of 12 ° C for 2 hours to obtain a rubber. Shaped body. The obtained molded body was cut into a width of 100 mm, a depth of 50 mm, and a height of 20 mm to measure the thermal conductivity. Example 5: Alumina (AS10, manufactured by Showa Denko Co., Ltd.) having an average particle diameter of 39 μm and a BET specific surface area of 0.5 m 2 /g, 580 g, and a vapor-phase carbon fiber having an average fiber diameter of 150 nm and an aspect ratio of 30 (VGCF- H, manufactured by Showa Denko Co., Ltd.) 12g was mixed with a Hensche honing machine for 1 second. The obtained composition containing alumina and fumed carbon fiber was charged with a commercially available polyfluorene oxide oil (TSE3070, manufactured by GE Toshiba Polyoxo Co., Ltd.) to a kneading machine (τ.Κ. HIVIS). MIX®, manufactured by Special Machine Chemical Co., Ltd., was kneaded at a rotation speed of 50 rpm for 1 minute. Thereafter, the mixture was placed in a mold by a centrifugal defoaming machine at a rotation speed of 450 rpm for 5 minutes, and then dried at a temperature of 120 ° C for 2 hours in a vacuum dryer to obtain a rubber-like formed body. The obtained molded body was cut into a width of 100 mm, a depth of 50 mm, and a height of 20 mm to measure the thermal conductivity. Example 6: An alumina having an average particle diameter of 39 μm η BET specific surface area of 55 m 2 /g (

A -24- (21) (21)1328018 AS10’昭和電工公司製）396g，與平均纖維徑l〇〇nm，長 寬比100之氣相法碳纖維（VGCF-S，昭和電工公司製） 4 g以H e n s c h e 1硏磨機混合1 〇秒。將含有所得之氧化鋁 及氣相法碳纖維之組成物充塡於市售之聚矽氧油（ TSE3070’ GE東芝聚矽氧公司製）l〇〇g，以捏合機（τ.κ HI VIS MIX®，特殊機化工業公司製）使旋轉速爲5 〇rpm 經1 〇分鐘捏合。其後，以離心脫泡機使旋轉速度成爲 4 5 Orpm經5分鐘處理裝塡於型箱後，以真空乾燥機，使 溫度爲1 20°C靜置2小時使之硬化獲得橡膠狀之成形體。 所得之成形體切割成寬100mm，深度50mm，高 2 0mm來測定導熱率。 實施例7 : 將平均粒徑39μπι，BET比表面積0.5m2/g之氧化鋁（ AS10，昭和電工公司製）392g，與平均纖維徑l〇〇nm，長 寬比1〇〇之氣相法碳纖維（VGCF-S，昭和電工公司製） 8g以Henschel硏磨機混合1〇秒。將含有所得之氧化鋁 及氣相法碳纖維之組成物充塡於市售之聚矽氧油（ TSE3070’ GE東芝聚矽氧公司製）i〇〇g，以捏合機（τ·κ· HIVIS MIX®，特殊機化工業公司製）使旋轉速爲50rpm 經1〇分鐘捏合。其後，以離心脫泡機，使旋轉速度成爲 45 0rpm經5分鐘處理裝塡於型箱後，以真空乾燥機，使 溫度爲120°C靜置2小時使之硬化獲得橡膠狀之成形體。 所得之成形體切割成寬100mm，深度50mm ,高 i -25- (22) 1328018 2 0 m m來測定導熱率。 if ' 實施例8 : 將平均粒徑39μηι，BET比表面積〇.5m2/g之氧化鋁（ AS10’昭和電工公司製）376g，與平均纖維徑15〇nm，長 寬比30之氣相法碳纖維（VGCF-H，昭和電工公司製） 24g以Henschel硏磨機混合10秒。將所得之含有氧化鋁 • 及氣相法^纖維之組成物充塡於市售之聚砂氧油（ TSE3070，GE東芝聚矽氧公司製）100g，以捏合機（τκ· HIVIS MIX® ’特殊機化工業公司製），使旋轉速爲50rpm 經1 0分鐘捏合。其後，以離心脫泡機，使旋轉速度成爲 45 Orpm經5分鐘處理裝塡於型箱後，以真空乾燥機，使 溫度爲1 2 0 °C靜置2小時使之硬化獲得橡膠狀之成形體。 所得1之成形體切割成寬l〇〇mm，深度50mm，高 2 0mm來測定導熱率。 比較例1: κ 將平均粒徑39μπι ’ BET比表面積〇.5m2/g之氧化鋁（ AS10’昭和電工公司製）400g以Henschel硏磨機混合 1〇秒後，充塡於市售之聚矽氧油（TSE3070，GE東芝聚 矽氧公司製）100g，以捏合機（T.K. HIVIS MIX®，特殊 機化工業公司製），使旋轉速爲50rpm經10分鐘捏合。 其後’以離心脫泡機，使旋轉速度成爲4 5 Or pm經5分鐘 處理裝塡於型箱後，以真空乾燥機，使溫度爲120°C靜置 •26· (24) 1328018 比較例4 : 將平均纖維徑lOOnm，長寬比100之氣; VGCF-S，B召和電工公司製）8g以Henschel 10秒後，充塡於市售之聚矽氧油（TSE3070 矽氧公司製）l〇〇g，以捏合機（T.K. HIVIS 機化工業公司製）使旋轉速爲5 Orpin經10 : 後’以離心脫泡機，使旋轉速度成爲450rpm 理裝塡於型箱後，以真空乾·燥機，使溫度爲 小時使之硬化獲得橡膠狀之成形體。所得之月 寬100mm，深度50mm，高20mm來測定導熱 :目法碳纖維（ 硏磨機混合 ，GE東芝聚 MIX®，特殊 子鐘捏合。其 經5分鐘處 1 2 0 °C靜置 2 ζ形體切割成 率。A -24- (21) (21) 1328018 396 g of AS10's Showa Denko Co., Ltd., and gas-phase carbon fiber (VGCF-S, manufactured by Showa Denko Co., Ltd.) having an average fiber diameter of 10 nm and an aspect ratio of 100 g 4 g Mix 1 sec. with a H ensche 1 honing machine. The composition containing the obtained alumina and fumed carbon fiber was charged to a commercially available polyfluorene oxide (TSE3070' GE Toshiba Polyoxo Co., Ltd.) l〇〇g to a kneader (τ.κ HI VIS MIX) ®, manufactured by Special Machine Chemical Co., Ltd.) kneading at a rotation speed of 5 rpm for 1 minute. Thereafter, the centrifugal defoaming machine was rotated at a speed of 45 rpm for 5 minutes, and then placed in a mold box, and then vacuum-dried at a temperature of 1200 ° C for 2 hours to be hardened to obtain a rubber-like shape. body. The obtained molded body was cut into a width of 100 mm, a depth of 50 mm, and a height of 20 mm to measure the thermal conductivity. Example 7: 392 g of alumina (AS10, manufactured by Showa Denko Co., Ltd.) having an average particle diameter of 39 μm and a BET specific surface area of 0.5 m 2 /g, and a vapor-phase carbon fiber having an average fiber diameter of 10 nm and an aspect ratio of 1 Å. (VGCF-S, manufactured by Showa Denko Co., Ltd.) 8 g was mixed in a Henschel honing machine for 1 second. The composition containing the obtained alumina and the gas-phase carbon fiber is filled with a commercially available polyoxyxene oil (TSE3070' GE Toshiba Polyoxo Co., Ltd.) i〇〇g, which is a kneading machine (τ·κ·HIVIS MIX). ®, manufactured by Special Machine Chemical Co., Ltd.) kneaded at a rotation speed of 50 rpm over 1 minute. Thereafter, the mixture was centrifuged at a rotation speed of 45 rpm for 5 minutes, and then placed in a mold box, and then vacuum-dried at a temperature of 120 ° C for 2 hours to be hardened to obtain a rubber-like molded body. . The obtained molded body was cut into a width of 100 mm, a depth of 50 mm, and a height of i -25 - (22) 1328018 2 0 m to measure the thermal conductivity. If 'Example 8: 376 g of alumina having an average particle diameter of 39 μm, a BET specific surface area of 55 m 2 /g (manufactured by AS 10 'Showa Denko Co., Ltd.), and a vapor-phase carbon fiber having an average fiber diameter of 15 〇 nm and an aspect ratio of 30 (VGCF-H, manufactured by Showa Denko) 24 g was mixed in a Henschel honing machine for 10 seconds. The obtained composition containing the alumina and the gas phase method was filled with a commercially available polysilicic acid (TSE3070, manufactured by GE Toshiba Polyoxo Co., Ltd.) 100 g as a kneading machine (τκ·HIVIS MIX® 'special Machine Engineering Co., Ltd.), kneading at a rotation speed of 50 rpm over 10 minutes. Thereafter, the mixture was centrifuged at a centrifugal speed of 45 rpm for 5 minutes, and then placed in a mold box, and then allowed to stand at a temperature of 120 ° C for 2 hours to be hardened to obtain a rubbery shape. Shaped body. The molded body of the obtained 1 was cut into a width of 10 mm, a depth of 50 mm, and a height of 20 mm to measure the thermal conductivity. Comparative Example 1: κ 400 g of alumina having an average particle diameter of 39 μm ' BET specific surface area 〇.5 m 2 /g (manufactured by AS 10' Showa Denko Co., Ltd.) was mixed in a Henschel honing machine for 1 sec., and then charged with a commercially available polypethane. Oxygen oil (TSE3070, manufactured by GE Toshiba Polymer Co., Ltd.) was kneaded by a kneading machine (TK HIVIS MIX®, manufactured by Kekyo Kogyo Co., Ltd.) at a rotation speed of 50 rpm for 10 minutes. Thereafter, the centrifugal defoaming machine was used to rotate the rotating speed to 4 5 Or pm for 5 minutes, and then placed in a mold box, and the vacuum was dried at 120 ° C. • 26· (24) 1328018 Comparative Example 4 : An average fiber diameter of 100 nm, an aspect ratio of 100 gas; VGCF-S, B and an electrician company) 8 g of Henschel for 10 seconds, and then charged with commercially available polyoxylized oil (TSE3070 Oxygen Company) L〇〇g, using a kneading machine (TK HIVIS Machine Chemical Co., Ltd.) to make the rotation speed 5 Orpin after 10: After 'with a centrifugal defoamer, the rotation speed is 450 rpm. After the package is placed in the mold, it is dried in a vacuum. Drying machine, which is made to cure in a small temperature to obtain a rubber-like molded body. The obtained monthly width is 100mm, depth is 50mm, height is 20mm to measure heat conduction: mesh carbon fiber (honing machine mixing, GE Toshiba poly MIX®, special sub-clock kneading. It is still placed at 1 2 0 °C for 5 minutes. Cutting rate.

-28- (25) 1328018 [A —表 1]-28- (25) 1328018 [A — Table 1]

氧化鋁 充塡量 S 氣相法碳纖 維充塡量 σ 長寬比 塡充劑 總量 σ 樹脂量 g 導熱率 w/(m · k) 爲使導熱率成爲 10w/(m · k)之必要充 塡總量kg 實施例1 396 4 70 400 100 1.5 2.7 實施例2 380 20 70 400 100 2.5 1.6 實施例3 594 6 70 600 100 2.3 2.6 實施例4 380 20 30 400 100 2.8 1.4 實施例8 376 24 30 400 100 2.9 1.3 實施例5 588 12 30 600 100 2.6 2.3 實施例6 396 4 100 400 100 1.9 2.1 實施例7 392 8 100 400 100 2.6 1.7 比較例1 400 400 100 1.3 3.1 比較例2 600 600 100 1.9 3.2 比較例3 4 100 4 100 0.4 0.1 比較例4 8 100 8 100 1.2 0.1Alumina filling amount S Gas phase carbon fiber filling amount σ Aspect ratio 塡 filling amount σ Resin amount g Thermal conductivity w/(m · k) The necessary charge for making the thermal conductivity 10w/(m · k) Total amount of hydrazine Example 1 396 4 70 400 100 1.5 2.7 Example 2 380 20 70 400 100 2.5 1.6 Example 3 594 6 70 600 100 2.3 2.6 Example 4 380 20 30 400 100 2.8 1.4 Example 8 376 24 30 400 100 2.9 1.3 Example 5 588 12 30 600 100 2.6 2.3 Example 6 396 4 100 400 100 1.9 2.1 Example 7 392 8 100 400 100 2.6 1.7 Comparative Example 1 400 400 100 1.3 3.1 Comparative Example 2 600 600 100 1.9 3.2 Comparative Example 3 4 100 4 100 0.4 0.1 Comparative Example 4 8 100 8 100 1.2 0.1

由表1可知，在陶瓷僅添加氣相法碳纖維，於塡充劑 總量爲相同之物，而可得放熱性優異之成形體，而在不與 陶瓷配合之物則導熱率劣化爲自明。 又，與使導熱率爲10w/ ( m · k)而爲必要塡充劑總量 比較時，相對於超過3kg之比較例1及比較例2，在實施 例1〜8均成爲3kg以下，而使氣相法碳纖維與陶瓷一起 配合，可減輕欲達成設定之導熱率爲必要塡充劑總量而可 謀求成形體之輕量化，因此本發明之工業價値極大。 -29- (26)1328018 %As is apparent from Table 1, only the vapor-phase carbon fiber was added to the ceramic, and the total amount of the chelating agent was the same, and a molded body having excellent heat dissipation property was obtained, and the thermal conductivity was deteriorated to be self-evident when the material was not blended with the ceramic. In addition, when the thermal conductivity is 10 w/(m · k) and the total amount of the chelating agent is required, the comparative examples 1 and 2 are more than 3 kg, and the examples 1 to 8 are 3 kg or less. When the vapor-phase carbon fiber is blended together with the ceramic, the total amount of the heat-receiving agent to be achieved can be reduced, and the weight of the molded body can be reduced. Therefore, the industrial price of the present invention is extremely high. -29- (26) 1328018 %

實施例9 : 將纖維徑1 5〇nm，長寬比40之氣相法碌 電工公司製，VGCF-H )以球磨機經1分鐘粉 維徑l5〇nm，長寬比38之氣相法碳纖維（A ) 氣相法碳纖維（A ) 1 2g與氧化鋁（昭和電工: 1 〇 ) 2 8 8 g以H e n s c h e 1硏磨機經1 0秒混合後 售之二液型聚矽氧油（TSE3070，GE東芝聚形 l〇〇g，以捏合機（T.K. HIVIS MIX®，特殊機 製），使旋轉速爲50rpm經10分鐘捏合。其 脫泡機，使旋轉速度成爲450rpm經5分鐘處 箱後，以真空乾燥機，使溫度爲120°C靜置2 化獲得橡膠狀之成形體。所得之成形體切割成 深度50mm，高20mm來測定導熱率。 又，將氣相法碳纖維（A ) 1 2g與氧化鋁 公司製，AS- 1 0 ) 288g以Henschel硏磨機經 ，充塡於市售之聚乙二醇（三洋化成工業公司 )l〇〇g，以捏合機（T.K. HIVIS MIX®，特殊 司製），使旋轉速爲50rpm經10分鐘捏合。 型黏度計進行黏度測定。 實施例I 0 ·· 將纖維徑1 5〇nm，長寬比40之氣相法 電工公司製，VGCF-H)以球磨機經5分鐘粉Example 9: a gas phase carbon fiber having a fiber diameter of 15 〇 nm and an aspect ratio of 40, manufactured by Gas Phase Method Co., Ltd., VGCF-H), which has a powder diameter of l5 〇 nm and an aspect ratio of 38 in a ball mill for 1 minute. (A) Gas-phase carbon fiber (A) 1 2g and alumina (Showa Denko: 1 〇) 2 8 8 g Two-liquid polyoxyxane oil (TSE3070) sold in a H ensche 1 honing machine after 10 seconds , GE Toshiba polymorphism l〇〇g, with a kneading machine (TK HIVIS MIX®, special mechanism), the kneading speed is 50 rpm for 10 minutes. The defoaming machine makes the rotation speed 450 rpm after 5 minutes. The molded body was cut into a depth of 50 mm and a height of 20 mm by a vacuum dryer at a temperature of 120 ° C to obtain a rubber-like molded body. Further, the vapor-phase carbon fiber (A ) 1 2 g was used. AS- 1 0) 288g is made of Henschel honing machine and is filled with commercially available polyethylene glycol (Sanyo Chemical Industry Co., Ltd.) l〇〇g, with kneading machine (TK HIVIS MIX®, special The system was kneaded by rotating at a speed of 50 rpm for 10 minutes. The viscosity meter is used for viscosity measurement. Example I 0 ·· A gas phase method with a fiber diameter of 15 μm and an aspect ratio of 40. VGCF-H) was passed through a ball mill for 5 minutes.

:纖維（昭和 碎，獲得纖 。將所得之 &amp;司製，Αεί ， 充塡 於市 氧公司製） 化工業公司 後，以離心 理裝塡於型 小時使之硬 寬 1 0 0 m m， (昭和電工 1 〇秒混合後 製 PEG-200 機化工業公 其後，以B 纖維（昭和 碎，獲得纖 -30- (27) (27)1328018 維徑1 5 0 n m，長寬比3 3之氣相法碳纖維（B )。所得之氣 相法碳纖維（B ) 12g與氧化鋁（昭和電工公司製，AS-10 )2 8 8 g以H e n s c h e 1硏磨機經1 0秒混合後，充塡於市售 之二液型聚矽氧油（TSE3〇7〇，GE東芝聚矽氧公司製） 】〇〇g，以捏合機（T.K. HIVIS MIX®，特殊機化工業公司 製），使旋轉速爲50rpm經10分鐘捏合。其後，以離心 脫泡機，使旋轉速度成爲45 Orpm經5分鐘處理裝塡於型 箱後，以真空乾燥機，使溫度爲120°C靜置2小時使之硬 化獲得橡膠狀之成形體。所得之成形體切割成寬1 00mm， 深度50mm，高20mm來測定導熱率。 又，將氣相法碳纖維（B) llg與氧化鋁（昭和電工 公司製，AS-10) 288g以Henschel硏磨機經1〇秒混合後 ，充塡於市售之聚乙二醇（三洋化成工業公司製PEG-200 )l〇〇g，以捏合機（T.K. HIVIS MIX®，特殊機化工業公 司製），使旋轉速爲50rpm經10分鐘捏合。其後，以b 型黏度計進行黏度測定。 實施例U : 將纖維徑150n m，長寬比40之氣相法碳纖維（昭和 電工公司製，VGCF-H )以球磨機經1〇分鐘粉碎，獲得纖 維徑150nm，長寬比28之氣相法碳纖維（C)。將所得之 氣相法碳纖維（C ) 12g與氧化鋁（昭和電工公司製，AS-10) 288g以Henschel硏磨機經10秒混合後，充塡市售 之二液型聚矽氧油（TSE3070，GE東芝聚矽氧公司製） -31 - (28) (28)1328018 l〇〇g，以捏合機（T.K. HIVIS MIX®，特殊機化工業公司 製）’使旋轉速爲5〇rpm經ι〇分鐘捏合。其後，以離心 脫泡機’使旋轉速度成爲450rpm經5分鐘處理裝塡於型 箱後’以真空乾燥機’使溫度爲1 20 °C靜置2小時使之硬 化獲得橡膠狀之成形體。所得之成形體切割成寬1 00mm， 深度50mm，高20mm來測定導熱率。 又’將氣相法碳纖維（C) l2g與氧化鋁（昭和電工 公司製’ AS-10) 288g以Henschel硏磨機經1〇秒混合後 ，充塡於市售之聚乙二醇（·三洋化成工業公司製PEG_2〇〇 )100g，以捏合機（T.K. HIVIS MIX®，特殊機化工業公 司製），使旋轉速爲5〇rpm經10分鐘捏合。其後，以B 型黏度計進行黏度測定。 實施例1 2 : 將纖維徑150nm’長寬比4〇之氣相法碳纖維（昭和 電工公司製’ VGCF-H)以球磨機經30分鐘粉碎，獲得纖 維徑150nm，長寬比24之氣相法碳纖維（D)。將所得之 氣相法碳纖維（D ) 12g與氧化鋁（昭和電工公司製，AS-10) 288g以Henschel硏磨機經1〇秒混合後，充塡於市 售之二液型聚矽氧油（TSE3070，GE東芝聚矽氧公司製） l〇〇g’以捏合機（T.K. HIVIS MIX®，特殊機化工業公司 製），使旋轉速爲50rpm經10.分鐘捏合。其後，以離心 脫泡機’使旋轉速度成爲450rpm經5分鐘處理裝塡於型 相後’以真空乾;fel機’使溫度爲120°C靜置2小時使之硬 -32- (29) (29)1328018 化獲得橡膠狀之成形體。所得之成形體切割成寬l00mm， 深度50mm，高20mm來測定導熱率。 又’將氣相法碳纖維（D)】2g與氧化鋁（昭和電工 公司製’ AS-10) 288g以Henschel硏磨機經1〇秒混合後 ’充塡市售之聚乙二醇（三洋化成工業公司製PEG-2 00 ) WOg，以捏合機（T.K. HIVIS MIX®，特殊機化工業公司 製）’使旋轉速爲50rpm經10分鐘捏合。其後，以B型 黏度計進fr黏度測定。 實施例1 3 : 將纖維徑150nm，長寬比40之氣相法碳纖維（昭和 電工公司製’ VGCF-H )以球磨機經60分鐘粉碎，獲得纖 維徑150nm’長寬比20之氣相法碳纖維（E)。將所得之 氣相法碳纖維（E ) 12g與氧化鋁（昭和電工公司製，AS-1 0 ) 288g以Henschel硏磨機經10秒混合後，充塡於市 售之二液型聚矽氧油（TSE3070，GE東芝聚矽氧公司製） l〇〇g，以捏合機（T.K. HIVIS MIX®，特殊機化工業公司 製），使旋轉速爲50rpm經10分鐘捏合。其後，以離心 脫泡機，使旋轉速度成爲450rpm經5分鐘處理裝塡於型 箱後，以真空乾燥機，使溫度爲120°C靜置2小時使之硬 化獲得橡膠狀之成形體。所得之成形體切割成寬1 00mm， 深度50mm，高20mm來測定導熱率》 又，將氣相法碳纖維（E) 12g與氧化鋁（昭和電工 公司製’ AS-10) 288g以Henschel硏磨機經1〇秒混合後 -33- (30) (30)1328018 ，充塡於市售之聚乙二醇（三洋化成工業公司製PEG-200 )l〇〇g，以捏合機（Τ·Κ. HIVIS MIX®，特殊機化工業公 司製），使旋轉速爲50rpm經10分鐘捏合。其後，以b 型黏度計進行黏度測定。 實施例1 4 : 將纖維徑1 5 0 n m，長寬比4 0之氣相法碳纖維（昭和 電工公司製，VGCF-H )以球磨機經60分鐘粉碎，獲得纖 維徑150nm，長寬比20之氣相法碳纖維（E)。將所得之 氣相法碳纖維（E ) 8g與氮化硼（昭和電工公司製，EX ) 192g以Henschel硏磨機經10秒混合後，充塡於市售之 二液型聚矽氧油（TSE3070，GE東芝聚矽氧公司製）100g ，以捏合機（T.K. HI VIS MIX®，特殊機化工業公司製） ，使旋轉速爲5 0 r p m經1 0分鐘捏合。其後，以離心脫泡 機’使旋轉速度成爲450rpm經5分鐘處理裝塡於型箱後 ，以真空乾燥機，使溫度爲120°C靜置2小時使之硬化獲 得橡膠狀之成形體。所得之成形體切割成寬l〇〇mm，深度 50mm，高20mm來測定導熱率。 又’將氣相法碳纖維（E) 8g與氮化硼（昭和電工公 司製，EX) 192g以Henschel硏磨機經1〇秒混合後，充 塡於市售之聚乙二醇（三洋化成工業公司製PEG_200 ) l〇〇g，以捏合機（T.K. HIVIS MIX®，特殊機化工業公司 製），使旋轉速爲50rpm經10分鐘捏合。其後，以b型 黏度計進行黏度測定。 -34- (32) (32)1328018 氮化硼及氣相法碳纖維之組成物（E)充塡於市售之聚矽 氧油（TSE3070，GE東芝聚矽氧公司製）l〇〇g，以捏合機 (T.K. HIVIS MIX®，特殊機化工業公司製），使旋轉速 爲50rpm經10分鐘捏合。其後，以離心脫泡機，使旋轉 速度成爲45 Orpm經5分鐘處理裝塡於型箱後，以真空乾 燥機，使溫度爲1 20 °C靜置2小時使之硬化獲得橡膠狀之 成形體。所得之成形體切割成寬100mm，深度50mm，高 2 0 m m來測定導熱率。 又，將氮化硼（昭和電工公司製，EX) 192g，與纖維 徑150nm長寬比40之氣相法碳纖維（VGCF_H，昭和電工 公司製）8g充塡於市售之聚乙二醇（三洋化成工業公司製 PEG-200) l〇〇g，以捏合機（T.K. HIVIS MIX®，特殊機 化工業公司製），使旋轉速爲50rpm經10分鐘捏合。其 後，以B型黏度計進行黏度測定。: Fiber (Showa shredded, obtained fiber. The resulting &amp; system, Α εί, filled with the company made by the company Oxygen Co., Ltd.), after the chemical industry company, centrifuged to fit the hour to make it a hard width of 100 mm, ( Showa Denko 1 〇 second mixed PEG-200 machine industry, followed by B fiber (Showa broken, obtained fiber -30- (27) (27) 1328018 diameter 150 nm, aspect ratio 3 3 Vapor-processed carbon fiber (B). The obtained vapor-phase carbon fiber (B) 12 g and alumina (AS-10, manufactured by Showa Denko Co., Ltd.) 2 8 8 g were mixed in a H ensche 1 honing machine for 10 seconds, and then charged.市 , , 市 市 , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , , The mixture was kneaded at a speed of 50 rpm for 10 minutes. Thereafter, the mixture was centrifuged at a centrifugal speed of 45 rpm for 5 minutes, and then placed in a mold box, and then allowed to stand at a temperature of 120 ° C for 2 hours in a vacuum dryer. The rubber-like molded body was obtained by hardening, and the obtained molded body was cut into a width of 100 mm, a depth of 50 mm, and a height of 20 mm to measure the thermal conductivity. The vapor-phase carbon fiber (B) llg and alumina (AS-10, manufactured by Showa Denko Co., Ltd.) were mixed in a Henschel honing machine for 1 sec., and then filled with commercially available polyethylene glycol (Sanyo Chemical Industry Co., Ltd.). The PEG-200) was kneaded by a kneading machine (TK HIVIS MIX®, manufactured by Kosei Kogyo Co., Ltd.) at a rotation speed of 50 rpm for 10 minutes, and then the viscosity was measured by a b-type viscometer. Example U: A fumed carbon fiber (VGCF-H, manufactured by Showa Denko Co., Ltd.) having a fiber diameter of 150 nm and an aspect ratio of 40 was pulverized in a ball mill for 1 minute to obtain a vapor-phase carbon fiber having a fiber diameter of 150 nm and an aspect ratio of 28. (C) The obtained vapor-phase carbon fiber (C) 12 g and 288 g of alumina (AS-10, manufactured by Showa Denko Co., Ltd.) were mixed in a Henschel honing machine for 10 seconds, and then the commercially available two-liquid type polyfluorene was charged. Oxygen oil (TSE3070, manufactured by GE Toshiba Polyoxo Co., Ltd.) -31 - (28) (28) 1328018 l〇〇g, with a kneading machine (TK HIVIS MIX®, manufactured by Special Machine Chemical Co., Ltd.) 〇 rpm is kneaded by ι〇 minutes. Thereafter, the centrifugal defoamer is used to make the rotation speed 450 rpm and process for 5 minutes. After the flask 'vacuum dryer' so that the temperature of 1 20 ° C standing for 2 hours so as to obtain the hardening of the rubber-like molded article. The resulting molded product was cut into a width of 1 00mm, depth 50mm, 20mm high thermal conductivity is measured. In addition, '2g of fumed carbon fiber (C) and 288g of alumina (AS-10 manufactured by Showa Denko Co., Ltd.) were mixed in a Henschel honing machine for 1 second, and then filled with commercially available polyethylene glycol (· Sanyo) 100 g of PEG 2 (manufactured by Kasei Kogyo Co., Ltd.) was kneaded by a kneading machine (TK HIVIS MIX®, manufactured by Kekyo Kogyo Co., Ltd.) at a rotation speed of 5 rpm for 10 minutes. Thereafter, the viscosity was measured using a B-type viscometer. Example 1 2: A gas phase carbon fiber ("VGCF-H" manufactured by Showa Denko Co., Ltd.) having a fiber diameter of 150 nm' and an aspect ratio of 4 Å was pulverized in a ball mill for 30 minutes to obtain a gas phase method having a fiber diameter of 150 nm and an aspect ratio of 24 Carbon fiber (D). 12 g of the obtained vapor-phase carbon fiber (D) and 288 g of alumina (AS-10, manufactured by Showa Denko Co., Ltd.) were mixed in a Henschel honing machine for 1 sec., and then filled with a commercially available two-liquid polyphthalic acid oil. (TSE3070, manufactured by GE Toshiba Polyoxane Co., Ltd.) l〇〇g' was kneaded by a kneading machine (TK HIVIS MIX®, manufactured by Kekyo Kogyo Co., Ltd.) at a rotation speed of 50 rpm for 10 minutes. Thereafter, the centrifugal defoamer was used to make the rotation speed to 450 rpm and the mold was applied to the mold after 5 minutes of treatment. The vacuum was dried; the fel machine was allowed to stand at 120 ° C for 2 hours to make it hard-32- (29 (29) 1328018 A rubber-like formed body was obtained. The obtained molded body was cut into a width of 100 mm, a depth of 50 mm, and a height of 20 mm to measure the thermal conductivity. In addition, 2 g of fumed carbon fiber (D) and 288 g of alumina (AS-10 manufactured by Showa Denko Co., Ltd.) were mixed in a Henschel honing machine for 1 sec., and then filled with polyethylene glycol (Sanyo Chemical Co., Ltd.) PEG-2 00 ) WOg manufactured by Industrial Co., Ltd. was kneaded by a kneading machine (TK HIVIS MIX®, manufactured by Kekyo Kogyo Co., Ltd.) at a rotation speed of 50 rpm for 10 minutes. Thereafter, the fr viscosity was measured by a B-type viscosity meter. Example 1 3: A vapor-phase carbon fiber having a fiber diameter of 150 nm and an aspect ratio of 40 (VGCF-H manufactured by Showa Denko Co., Ltd.) was pulverized in a ball mill for 60 minutes to obtain a vapor-phase carbon fiber having a fiber diameter of 150 nm' aspect ratio of 20. (E). 12 g of the obtained fumed-process carbon fiber (E) and 288 g of alumina (AS-1 0 manufactured by Showa Denko Co., Ltd.) were mixed in a Henschel honing machine for 10 seconds, and then filled with a commercially available two-liquid polyphthalic acid oil. (TSE3070, manufactured by GE Toshiba Polyoxane Co., Ltd.) l〇〇g, kneaded by a kneading machine (TK HIVIS MIX®, manufactured by Special Machine Chemical Co., Ltd.) at a rotation speed of 50 rpm for 10 minutes. Then, the mixture was placed in a mold by a centrifugal defoaming machine at a rotation speed of 450 rpm for 5 minutes, and then allowed to stand at a temperature of 120 ° C for 2 hours in a vacuum dryer to be hardened to obtain a rubber-like molded body. The obtained molded body was cut into a width of 100 mm, a depth of 50 mm, and a height of 20 mm to measure the thermal conductivity. Further, 12 g of the vapor-phase carbon fiber (E) and alumina (manufactured by Showa Denko's AS-10) 288 g were used as a Henschel honing machine. After mixing for 1 second, -33- (30) (30) 1328018, filled with commercially available polyethylene glycol (PEG-200 manufactured by Sanyo Chemical Industries Co., Ltd.) l〇〇g, with a kneading machine (Τ·Κ. HIVIS MIX®, manufactured by Kosei Kogyo Co., Ltd., was kneaded at a rotation speed of 50 rpm for 10 minutes. Thereafter, the viscosity was measured by a b-type viscometer. Example 1 4: A gas-phase carbon fiber (VGCF-H, manufactured by Showa Denko Co., Ltd.) having a fiber diameter of 150 nm and an aspect ratio of 40 was pulverized in a ball mill for 60 minutes to obtain a fiber diameter of 150 nm and an aspect ratio of 20 Gas phase carbon fiber (E). 8 g of the obtained vapor-phase carbon fiber (E) and 192 g of boron nitride (EX, manufactured by Showa Denko Co., Ltd.) were mixed in a Henschel honing machine for 10 seconds, and then filled with a commercially available two-liquid type polyoxygenated oil (TSE3070). 100 g of GE Toshiba Polyoxane Co., Ltd. was kneaded by a kneading machine (TK HI VIS MIX®, manufactured by Kekyo Kogyo Co., Ltd.) at a rotational speed of 50 rpm over 10 minutes. Thereafter, the mixture was placed in a mold by a centrifugal defoaming machine at a rotation speed of 450 rpm for 5 minutes, and then dried in a vacuum dryer at a temperature of 120 ° C for 2 hours to obtain a rubber-like molded body. The obtained molded body was cut into a width of 10 mm, a depth of 50 mm, and a height of 20 mm to measure the thermal conductivity. In addition, 8 g of gas-phase carbon fiber (E) and 192 g of boron nitride (EX, manufactured by Showa Denko Co., Ltd.) were mixed in a Henschel honing machine for 1 sec., and then filled with commercially available polyethylene glycol (Sanyo Chemical Industry Co., Ltd.) The company's PEG_200) l〇〇g was kneaded by a kneading machine (TK HIVIS MIX®, manufactured by Special Machine Chemical Co., Ltd.) at a rotation speed of 50 rpm for 10 minutes. Thereafter, the viscosity was measured by a b-type viscometer. -34- (32) (32) 1328018 The composition of boron nitride and fumed carbon fiber (E) is filled with commercially available polyoxyxide oil (TSE3070, manufactured by GE Toshiba Polymer Co., Ltd.) l〇〇g, The kneading machine (TK HIVIS MIX®, manufactured by Kekyo Kogyo Co., Ltd.) was kneaded at a rotation speed of 50 rpm for 10 minutes. Thereafter, the centrifugal defoaming machine was used, and the rotation speed was changed to 45 O rpm for 5 minutes, and then it was placed in a mold box, and then vacuum-dried at a temperature of 1 20 ° C for 2 hours to be hardened to obtain a rubber-like shape. body. The obtained molded body was cut into a width of 100 mm, a depth of 50 mm, and a height of 20 mm to measure the thermal conductivity. In addition, 192 g of boron nitride (EX, manufactured by Showa Denko Co., Ltd.) and 8 g of gas phase carbon fiber (VGCF_H, manufactured by Showa Denko Co., Ltd.) having a fiber diameter of 150 nm and an aspect ratio of 40 were filled with commercially available polyethylene glycol (Sanyo). PEG-200, manufactured by Kasei Kogyo Co., Ltd., was kneaded by a kneading machine (TK HIVIS MIX®, manufactured by Kosei Kogyo Co., Ltd.) at a rotation speed of 50 rpm for 10 minutes. Thereafter, the viscosity was measured by a B-type viscometer.

-36- (33) 1328018 [表2] 塡充劑 粉碎時間 長寬比 導熱率 黏度(Pa · s) (分） (W/(m · k)) lOrpm lOOrpm 實施例9 氧化鋁 1 38 1.7 11 13 實施例10 氧化鋁 5 33 1.6 11 30 實施例11 氧化鋁 10 28 1.6 17 29 實施例12 氧化鋁 30 24 1.7 11 23 實施例13 氧化鋁 60 20 1.6 8 19 比較例5 氧化鋁 0 40 1.6 26 37 實施例14 氮化硼 60 20 3.0 29 38 比較例ό 氮化硼 0 40 2.0 50 65-36- (33) 1328018 [Table 2] Filler pulverization time aspect ratio Thermal conductivity viscosity (Pa · s) (minutes) (W / (m · k)) lOrpm lOOrpm Example 9 Alumina 1 38 1.7 11 13 Example 10 Alumina 5 33 1.6 11 30 Example 11 Alumina 10 28 1.6 17 29 Example 12 Alumina 30 24 1.7 11 23 Example 13 Alumina 60 20 1.6 8 19 Comparative Example 5 Alumina 0 40 1.6 26 37 Example 14 Boron Nitride 60 20 3.0 29 38 Comparative Example 氮化 Boron Nitride 0 40 2.0 50 65

由表2可知，使長寬比減低之VGCF及氧化鋁予以混It can be seen from Table 2 that VGCF and alumina with a reduced aspect ratio are mixed.

合之系（實施例9〜實施例13)與使長寬比40之VGCF 及氧化鋁混合之系（比較例5 )加以比較，在不減低導熱 率下可使流動性大幅改善爲自明。又，藉由使長寬比減低 之VGCF及氮化硼混合之系（實施例Η)與長寬比40之 v G C F及氮化硼混合之系（比較例6 )加以比較，在不減 低導熱率下可使流動性大幅改善。因此，本發明之複合材 料用組成物，與使用於習知放熱材料之充塡材比較充塡量 可增加’因可獲得放熱性優異之放熱材料，故工業價値極 高。 實施例1 5 : -37- (34) (34)1328018 在氧化鋁（AS-10，昭和電工公司製）96質量份以清 漆A之樹脂固形成分換算於5.4質量份添加乙醇12.6質 量份予以擅拌，添加充分溶解之溶液使變形苯酣樹脂固形 成分成爲4質量％，以行星式混合機經30分鐘捏合。進而 ，在2800°C添加石墨化之氣相法碳纖維（VGCF-H，昭和 電工公司製；平均纖維徑150nm，長寬比40) 4質量份進 行捏合。將捏合物以真空乾燥機80°C經2小時乾燥，將乙 醇除去。進而以真空乾燥機在180 °C保持10分後，在 15CTC保持2小時予以硬化_。將所得之氧化鋁-氣相法碳纖 維複合組成物（A ) 300g以市售之二液型聚矽氧油（ TSE3070，GE東芝聚矽氧公司製）l〇〇g，捏合機（τ.κ. HIVIS MIX®，特殊機化工業公司製）在5〇rpm經之旋轉 速度經10分鐘捏合。其後，以離心脫泡機，在45 Orpin經 之旋轉速度經5分鐘處理裝塡於型箱後，以真空乾燥機， 成爲溫度120°C靜置2小時使之硬化獲得橡膠狀之成形體 。所得之成形體切割成寬100mm，深度50mm，高20mm 來測定導熱率。又，電子顯微鏡觀察結果係如第1圖及第 2圖所示。 將氧化鋁，氣相法碳纖維複合粉（A) 3 00g充塡於市 售之聚乙二醇（三洋化成工業公司製PEG-200 ) 100g，以 捏合機（Τ.Κ. HIVIS MIX®，特殊機化工業公司製），在 50rpm經之旋轉速度經1〇分鐘捏合。其後，以B型黏度 計進行黏度測定》 -38- (35) (35)1328018 實施例1 6 : 在氧化鋁（AS-10，昭和電工公司製）96質量份以清 漆A之樹脂固形成分換算於5.4質量份添加乙醇12.6質 量份予以攪拌，添加充分溶解之溶液以使變形苯酚樹脂固 形成分成爲7質量％，以行星式混合機經3 〇分鐘捏合。進 而’添加在2800°C石墨化之氣相法碳纖維（VGCF-H，昭 和電工公司製平均纖維徑I50nm，長寬比40) 4質量份予 以捏合。將捏合物以真空乾燥機於80°C經2小時乾燥，將 乙醇除去。進而以真空乾燥·機在180°C保持1〇分後，在 1 50°C保持2小時使之硬化。將所得之氧化鋁，氣相法碳 纖維複合組成物（B ) 300 g充塡於市售之二液型聚矽氧油 (TSE3070，GE東芝聚矽氧公司製）l〇〇g，以捏合機（ T.K. HIVIS MIX®，特殊機化工業公司製）在50rpm經之 旋轉速度經1 〇分鐘捏合。其後，以離心脫泡機，使旋轉 速度成爲45 Orpm經5分鐘處理裝塡於型箱後，以真空乾 燥機，使溫度爲120°C靜置2小時使之硬化獲得橡膠狀之 成形體。所得之成形體切割成寬100mm，深度50mm，高 20mm來測定導熱率。又，將電子顯微鏡觀察結果如第3 圖及第4圖所示。 將氧化鋁，氣相法碳纖維複合粉（B) 3 00g充塡於市 售之聚乙二醇（三洋化成工業公司製PEG-200 ) l〇〇g，以 捏合機（T.K. HIVIS MIX®，特殊機化工業公司製），在 5 Orpm經之旋轉速度經〗〇分鐘捏合。其後，以B型黏度 計進行黏度測定。 -39- (36) (36)1328018 實施例1 7 : 在氧化鋁（AS-10，昭和電工公司製）96質量份以清 漆A之樹脂固形成分換算於5.4質量份添加乙醇12_6質 量份予以攪拌，添加充分溶解之溶液使變形苯酚樹脂固形 成分成爲1 0質量％，以行星式混合機經3 0分鐘捏合。進 而’添加在2800°C已石墨化之氣相法碳纖維（VGCF-H， 昭和電工公司製：平均纖維徑150nm，長寬比40 ) 4質量 份予以捏合。將捏合物以真空乾燥機於8 0 °C經2小時乾燥 ，將乙醇除去。進而以真空乾燥機在180 °C保持10分後， 在1 5 0 °C保持2小時使之硬化。將所得之氧化鋁，氣相法 碳纖維複合組成物（C) 300g充塡於市售之二液型聚砂氧 油（TSE3070，GJE東芝聚矽氧公司製）i〇〇g，捏合機（ T.K. HIVIS MIX®，特殊機化工業公司製），以5〇rpm經 之旋轉速度經10分鐘捏合。其後，以離心脫泡機，使旋 轉速度成爲450rpm經5分鐘處理裝塡於型箱後，在真空 乾燥機，使溫度爲120 °C靜置2小時使之硬化獲得橡膠狀 之成形體。所得之成形體切割成寬100mm，深度50mm , 高20mm來測定導熱率。又，電子顯微鏡觀察結果如第5 圖及第6圖所示。 使氧化銘，氣相法碳纖維複合粉（C) 300g充塡於市 售之聚乙二醇（三洋化成工業公司製PEG-200) l〇〇g,捏 合機（T.K. HIVIS MIX®，特殊機化工業公司製），在 5 Or pm經之旋轉速度經10分鐘捏合。其後，以b型黏度 -40- (38) 1328018 [表3] 苯酚樹脂固形分濃度 m 黏度（Pa · s) 質量％ w ( m · k) 1 0 r p m 1 OOrpm 實施例1 5 4 1.6 16 3 實施例1 6 7 1.4 18 3 實施例1 7 10 1.3 22 5 比較例7 0 0.8 6 2 比較例5 0 1.6 26 3 7The combination (Examples 9 to 13) was compared with a system in which VGCF and alumina of an aspect ratio of 40 were mixed (Comparative Example 5), and the fluidity was greatly improved to be self-evident without lowering the thermal conductivity. Further, by comparing the VGCF and boron nitride mixed system (Example Η) having an aspect ratio reduced with the V GCF and boron nitride mixed with an aspect ratio of 40 (Comparative Example 6), heat conduction is not reduced. The rate can greatly improve the liquidity. Therefore, the composition for a composite material of the present invention can be increased in comparison with a chargeable material used for a conventional heat-releasing material. The industrial price is extremely high because the heat-releasing material having excellent heat dissipation property can be obtained. Example 1 5 : -37- (34) (34) 1328018 In an amount of 96 parts by mass of alumina (AS-10, manufactured by Showa Denko Co., Ltd.), the amount of the solid component of the varnish A was adjusted to 5.4 parts by mass, and 12.6 parts by mass of ethanol was added. After mixing, a sufficiently dissolved solution was added to make the solid component of the deformed benzoquinone resin 4% by mass, and kneaded by a planetary mixer for 30 minutes. Further, 4 parts by mass of graphitized gas phase carbon fiber (VGCF-H, manufactured by Showa Denko Co., Ltd.; average fiber diameter: 150 nm, aspect ratio: 40) was kneaded at 2,800 °C. The kneaded product was dried in a vacuum dryer at 80 ° C for 2 hours to remove ethanol. Further, after holding at a temperature of 180 ° C for 10 minutes in a vacuum dryer, it was cured at 15 CTC for 2 hours. 300 g of the obtained alumina-gas phase carbon fiber composite composition (A) was commercially available as a two-liquid polysulfonated oil (TSE3070, manufactured by GE Toshiba Polyoxo Co., Ltd.), kneading machine (τ.κ HIVIS MIX® (manufactured by Specialized Chemical Industry Co., Ltd.) was kneaded at a rotation speed of 5 rpm for 10 minutes. Thereafter, the mixture was placed in a mold at a rotation speed of 45 Orpin for 5 minutes by a centrifugal defoaming machine, and then dried in a vacuum dryer at a temperature of 120 ° C for 2 hours to obtain a rubber-like molded body. . The obtained molded body was cut into a width of 100 mm, a depth of 50 mm, and a height of 20 mm to measure the thermal conductivity. Further, the results of electron microscope observation are shown in Fig. 1 and Fig. 2 . 300 g of alumina, gas phase carbon fiber composite powder (A) was charged to 100 g of commercially available polyethylene glycol (PEG-200 manufactured by Sanyo Chemical Industries Co., Ltd.) to a kneading machine (Τ.Κ. HIVIS MIX®, special Kikken Co., Ltd.), kneaded at 50 rpm through a rotation speed of 1 minute. Thereafter, the viscosity was measured by a B-type viscometer. -38- (35) (35) 1328018 Example 1 6 : 96 parts by mass of alumina (AS-10, manufactured by Showa Denko) was used to form a resin of varnish A. In an amount of 12.6 parts by mass of 5.4 parts by mass of the added ethanol, the mixture was stirred, and a sufficiently dissolved solution was added so that the solid content of the deformed phenol resin was 7% by mass, and the mixture was kneaded by a planetary mixer for 3 minutes. Further, 4 parts by mass of a gas phase carbon fiber (VGCF-H, average fiber diameter I50 nm, aspect ratio 40, manufactured by Showa Denko Co., Ltd.) which was graphitized at 2,800 °C was added and kneaded. The kneaded product was dried in a vacuum dryer at 80 ° C for 2 hours to remove ethanol. Further, the mixture was kept at 180 ° C for 1 minute in a vacuum drying machine, and then cured at 190 ° C for 2 hours. The obtained alumina, vapor phase carbon fiber composite composition (B) 300 g was charged with a commercially available two-liquid polysulfonated oil (TSE 3070, manufactured by GE Toshiba Polyoxo Co., Ltd.) to a kneading machine. (TK HIVIS MIX®, manufactured by Special Machine Chemical Co., Ltd.) was kneaded at a rotation speed of 50 rpm for 1 minute. Thereafter, the mixture was centrifuged at a centrifugal speed of 45 rpm for 5 minutes, and then placed in a mold box, and then allowed to stand at a temperature of 120 ° C for 2 hours in a vacuum dryer to obtain a rubber-like molded body. . The obtained molded body was cut into a width of 100 mm, a depth of 50 mm, and a height of 20 mm to measure the thermal conductivity. Further, the results of observation by an electron microscope are shown in Figs. 3 and 4. Alumina, gas phase carbon fiber composite powder (B) 300 g is charged with commercially available polyethylene glycol (PEG-200 manufactured by Sanyo Chemical Industries Co., Ltd.) l〇〇g, with a kneading machine (TK HIVIS MIX®, special Machine Chemical Industry Co., Ltd.), kneaded at a rotation speed of 5 Orpm for 〇 minute. Thereafter, the viscosity was measured by a B-type viscosity meter. -39- (36) (36) 1328018 Example 1 7 : 96 parts by mass of alumina (AS-10, manufactured by Showa Denko Co., Ltd.) was stirred in an amount of 5.4 parts by mass of 8.5 parts by mass of ethanol added to the solid content of varnish A. A sufficiently dissolved solution was added to make the solid content of the deformed phenol resin 10% by mass, and kneaded by a planetary mixer for 30 minutes. Further, it was kneaded by adding 4 parts by mass of a vaporized carbon fiber (VGCF-H, manufactured by Showa Denko Co., Ltd.: average fiber diameter 150 nm, aspect ratio 40) which was graphitized at 2,800 °C. The kneaded product was dried in a vacuum dryer at 80 ° C for 2 hours to remove ethanol. Further, after holding at a temperature of 180 ° C for 10 minutes in a vacuum dryer, it was cured at 150 ° C for 2 hours. 300 g of the obtained alumina, vapor-phase carbon fiber composite composition (C) was charged with a commercially available two-liquid polyoxalate oil (TSE 3070, manufactured by Toshiba Polymer Co., Ltd.) i〇〇g, kneading machine (TK) HIVIS MIX® (manufactured by Special Machine Chemical Co., Ltd.) was kneaded at a rotation speed of 5 rpm for 10 minutes. Thereafter, the mixture was placed in a mold at a spinning speed of 450 rpm for 5 minutes by a centrifugal defoaming machine, and the mixture was allowed to stand at a temperature of 120 ° C for 2 hours in a vacuum dryer to be hardened to obtain a rubber-like molded body. The obtained molded body was cut into a width of 100 mm, a depth of 50 mm, and a height of 20 mm to measure the thermal conductivity. Further, the results of electron microscope observation are shown in Fig. 5 and Fig. 6. Oxidation, gas-phase carbon fiber composite powder (C) 300g is filled with commercially available polyethylene glycol (PEG-200 manufactured by Sanyo Chemical Industries Co., Ltd.) l〇〇g, kneading machine (TK HIVIS MIX®, special machine Co., Ltd.), kneaded at 5 Or pm for 10 minutes. Thereafter, the viscosity of b-type -40 - (38) 1328018 [Table 3] phenol resin solid concentration m viscosity (Pa · s) mass % w (m · k) 1 0 rpm 1 OO rpm Example 1 5 4 1.6 16 3 Example 1 6 7 1.4 18 3 Example 1 7 10 1.3 22 5 Comparative Example 7 0 0.8 6 2 Comparative Example 5 0 1.6 26 3 7

由表3可知在添加氣相法碳纖維之實施例1 5〜實施例 17，與不添加氣相法碳纖維之比較例7比較可提高導熱率 爲自明。又，添加氣相法碳纖維藉由苯酚樹脂與氧化鋁複 合化之實施例1 5〜實施例1 7，與將氣相法碳纖維與氧化 鋁以Henschel硏磨機混合之比較例5比較，黏度可大幅 減低爲自明。進而，藉由電子顯微鏡觀察結果可知，均係 氣相法碳纖維爲高分散使氧化鋁表面予以同樣地被覆，而 僅爲氣相法碳纖維之塊並無法觀察到。由該等可知，本發 明係至目前爲止爲放熱材料塡充劑之課題之導熱率提高與 黏度減低可一起大幅提高，工業價値爲極高。 【圖式簡單說明】 第1圖表示實施例1，2，4，6，7，8及比較例1中 氣相法碳纖維添加量與對陶瓷導熱比之關係圖，X爲陶瓷 之添加量，Y爲氣相法碳纖維之添加量。 -42- (39) (39)1328018 第2圖係在實施例1 5所得複合材料之電子顯微鏡照 片（1，〇〇〇 倍）。 第3圖係實施例1 5所得複合材料之電子顯微鏡照片 (3，5 0 0 倍）。 第4圖係實施例1 6所得複合材料之電子顯微鏡照片 (1，000 倍）。 第5圖係實施例1 6所得複合材料之電子顯微鏡照片 (3,500 倍）。 第6圖係實施例1 7所得複合材料之電子顯微鏡照片 (1，0 0 0 倍）。 第7圖係實施例1 7所得複合材料之電子顯微鏡照片 (3,500 倍）。 -43 -As is apparent from Table 3, in Examples 15 to 17 in which the vapor-phase carbon fibers were added, the thermal conductivity was improved as compared with Comparative Example 7 in which the vapor-phase carbon fibers were not added. Further, the addition of the vapor-phase carbon fiber by the phenol resin and the alumina composite Example 15 to Example 127, compared with the comparative example 5 in which the vapor-phase carbon fiber and the alumina were mixed in a Henschel honing machine, the viscosity was Significantly reduced self-evident. Further, as a result of observation by an electron microscope, it was found that the vapor phase carbon fibers were highly dispersed, and the alumina surface was similarly coated, and it was only observed as a vapor-phase carbon fiber block. As can be seen from the above, the present invention is an improvement in the thermal conductivity and the viscosity reduction which are the subject of the exothermic material squeezing agent up to now, and the industrial price is extremely high. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a view showing the relationship between the amount of carbon-phase carbon fiber added and the ratio of heat conductivity to ceramics in Examples 1, 2, 4, 6, 7, 8 and Comparative Example 1, and X is the amount of ceramic added. Y is the amount of carbon fiber added by the vapor phase method. -42- (39) (39) 1328018 Fig. 2 is an electron micrograph (1, 倍) of the composite material obtained in Example 15. Fig. 3 is an electron micrograph of the composite obtained in Example 1 (3,500 times). Fig. 4 is an electron micrograph (1,000 times) of the composite material obtained in Example 16. Fig. 5 is an electron micrograph (3,500 times) of the composite material obtained in Example 16. Fig. 6 is an electron micrograph of the composite material obtained in Example 1 (1,0 0 0). Fig. 7 is an electron micrograph (3,500 times) of the composite material obtained in Example 17. -43 -

Claims (1)

13280181328018 十、申請專利範圍 第94 14 1 746號專利申請案 中文申請專利範圍修正本 民國99年2月4曰修正 1. 一種複合材料用組成物，其爲含有碳材料及於表 面具有官能基之陶瓷，X. Patent Application No. 94 14 1 746 Patent Application Revision of Chinese Patent Application Revision of the Republic of China on February 4, 1999. 1. A composition for composite materials, which is a ceramic containing carbon material and having functional groups on the surface. , 其特徵爲，碳材料係選自平均纖維徑50〜500nm，長 寬比5〜1 000之氣相法碳纖維、碳奈米管、焦炭粉及石墨 粉所成群之至少一種，陶瓷係平均粒子徑0.3〜80μπι，比 表面積0.01〜15m2/g之陶瓷粒子，陶瓷係選自氧化鋁、氧 化鎂、氧化鋅、二氧化矽及氮化硼所成群之至少一種之化 合物。 2.如申請專利範圍第1項記載之複合材料用組成物 ’其中平均纖維徑50〜500nm，長寬比5以上不足40之 氣相法碳纖維係分散於陶瓷粉體中。The carbon material is selected from the group consisting of a gas phase carbon fiber having an average fiber diameter of 50 to 500 nm and an aspect ratio of 5 to 1,000, a carbon nanotube, a coke powder and a graphite powder, and an average ceramic particle. The ceramic particles having a diameter of 0.3 to 80 μm and a specific surface area of 0.01 to 15 m 2 /g, and the ceramics are at least one selected from the group consisting of alumina, magnesia, zinc oxide, ceria, and boron nitride. 2. The composition for a composite material according to the first aspect of the invention, wherein the vapor phase carbon fiber having an average fiber diameter of 50 to 500 nm and an aspect ratio of 5 or more and less than 40 is dispersed in the ceramic powder. 3 .如申請專利範圍第1項記載之複合材料用組成物 ’其中碳材料係氣相法碳纖維，陶瓷係氧化鋁或氮化硼。 4.如申請專利範圍第1項記載之複合材料用組成物 ’其含有平均纖維徑10〜500nm，長寬比5〜1〇〇〇之氣相 法碳纖維及陶瓷粒子，在該氣相法碳纖維及該陶瓷粒子透 過具有黏接性之高分子化合物，在該陶瓷粒子表面之至少 一部份附著該氣相法碳纖維。 5 ·如申請專利範圍第4項記載之複合材料用組成物 ’其中高分子化合物係選自苯酚樹脂、聚乙烯醇樹脂、咲 1328018 喃樹脂、纖維素樹脂、聚苯乙烯樹脂、聚醯亞胺樹脂、及 環氧樹脂所成群之至少一種。 6.如申請專利範圍第4項記載之複合材料用組成物 ，其中高分子化合物之配合量相對於陶瓷及氣相法碳纖維 之總量爲〇 · 1〜3 0質量％。 7·如申請專利範圍第1項記載之複合材料用組成物 ，其中碳材料之配合量爲陶瓷配合量之0.1〜20質量％。3. The composition for a composite material according to the first aspect of the invention, wherein the carbon material is a vapor-phase carbon fiber, a ceramic alumina or boron nitride. 4. The composition for a composite material according to the first aspect of the invention, which comprises a vapor-phase carbon fiber having an average fiber diameter of 10 to 500 nm and an aspect ratio of 5 to 1 Å, and a carbon fiber in the vapor phase method. And the ceramic particles pass through the polymer compound having adhesiveness, and the vapor-phase carbon fiber is adhered to at least a portion of the surface of the ceramic particle. 5. The composition for a composite material as described in claim 4, wherein the polymer compound is selected from the group consisting of a phenol resin, a polyvinyl alcohol resin, a ruthenium 1328018 resin, a cellulose resin, a polystyrene resin, and a polyimine. At least one of a group of a resin and an epoxy resin. 6. The composition for a composite material according to the fourth aspect of the invention, wherein the amount of the polymer compound is 〇1 to 30% by mass based on the total amount of the ceramic and the vapor-phase carbon fiber. 7. The composite material composition according to the first aspect of the invention, wherein the amount of the carbon material is 0.1 to 20% by mass based on the amount of the ceramic compound. 8·—種複合材料，其特徵爲，含有平均纖維徑1〇〜 5〇Onm’長寬比5〜1000之氣相法碳纖維及陶瓷粒子，在 該氣相法碳纖維及該陶瓷粒子透過具有黏接性之高分子化 合物，在該陶瓷粒子表面之至少一部份附著該氣相法碳纖 維之複合材料用組成物中配合高分子材料或油類，8. A composite material characterized by comprising a vapor-phase carbon fiber and ceramic particles having an average fiber diameter of 1 〇 5 〇 Onm' aspect ratio of 5 to 1000, wherein the vapor-phase carbon fiber and the ceramic particle are viscous a polymer compound in which a polymer material or an oil is blended in a composition for a composite material in which at least a part of the surface of the ceramic particle is adhered to the vapor-phase carbon fiber, 高分子材料或油類係選自脂肪族系樹脂、不飽和聚醋樹脂 、丙烯酸樹脂、甲基丙烯酸樹脂、乙烯酯樹脂、環氧樹脂 、聚砂氧樹脂、聚砂氧油、石油系油、及氟系油所成群之 至少一種，高分子材料或油類之配合量爲碳材料及陶瓷合 計量之1〜3 5質量。 9 .如申請專利範圍第8項記載之複合材料，其爲形成 成形體者。 10.如申請專利範圍第9項記載之複合材料，其中該 成形體爲薄片狀或薄膜狀。 11·如申請專利範圍第10項記載之複合材料，其中 該成形體係使用於放熱薄片。 12.如申請專利範圍第11項記載之複合材料，其中 -2- 1328018 該放熱薄片係使用於個人電腦。 13. 如申請專利範圍第11項記載之複合^ CJ何料’ 該放熱薄片係使用於遊戲機。 14. 如申請專利範圍第11項記載之複合材料 放熱薄片係使用於數位攝影機。 15. 如申請專利範圍第11項記載之複合材料 放熱薄片係使用於數位相機。 16. 如申請專利範圍第11項記載之複合材料 放熱薄片係使用於電視。 17. 如申請專利範圍第11項記載之複合材料 放熱薄片係使用於行動電話。 18_ —種如申請專利範圍第8項記載之複合材料之製 造方法，其特徵爲，將碳材料及陶瓷以乾式剪斷擾胃 所得組成物分散於高分子材料或油類者》 19. 一種如申請專利範圍第8項記載之複合材料之製 造方法，其特徵爲，對於平均纖維徑10〜500ηηι，長寬比 5〜1 000之氣相法碳纖維及陶瓷粒子，係使用具有黏接性 之高分子化合物將該氣相法碳纖維複合化於陶瓷粒子表面 ，使所得組成物分散於高分子材料或油類者。 其中 其中該 其中該 其中該 其中該The polymer material or oil is selected from the group consisting of an aliphatic resin, an unsaturated polyester resin, an acrylic resin, a methacrylic resin, a vinyl ester resin, an epoxy resin, a polyoxyn resin, a polysand oil, a petroleum oil, And at least one of the group of the fluorine-based oil, the amount of the polymer material or the oil is 1 to 35 masses of the total amount of the carbon material and the ceramic. 9. The composite material according to claim 8, wherein the composite material is formed into a molded body. 10. The composite material according to claim 9, wherein the formed body is in the form of a sheet or a film. 11. The composite material of claim 10, wherein the forming system is used for an exothermic sheet. 12. The composite material according to claim 11, wherein -2- 1328018 the exothermic sheet is used in a personal computer. 13. The composite material described in the eleventh application of the patent scope is used in a game machine. 14. The composite heat release sheet as described in claim 11 is used in a digital camera. 15. The composite heat release sheet described in claim 11 is used in a digital camera. 16. The composite heat release sheet of claim 11 is used in televisions. 17. The composite heat release sheet as described in claim 11 is used in mobile phones. 18_— A method for producing a composite material according to the eighth aspect of the invention, characterized in that a composition obtained by dispersing a carbon material and a ceramic by a dry shearing dislocation in a polymer material or an oil is used. The method for producing a composite material according to the eighth aspect of the invention is characterized in that, for a gas-fiber carbon fiber and ceramic particles having an average fiber diameter of 10 to 500 ηη, an aspect ratio of 5 to 1,000, the adhesiveness is high. The molecular compound combines the vapor-phase carbon fiber on the surface of the ceramic particle, and the obtained composition is dispersed in a polymer material or an oil. Where the one of the
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