201224168 、發明說明： 【發明所屬之技術領域】 應用 料ΪΓΓ提供—齡基複合材㈣作方法，_是關於 析m 奸在金屬級分佈不㈣銳鑄凝111過慢形成偏 。，進而達到成本低、高磨耗，適於運輸結構組件之 【先前技術】 近年要求郎能減碳潮流中，具輕量、高剛性、強度和 熱穩定性之金屬基複合材料的應用受到使用耐磨耗組件之 運輪業界_目。為提高金屬基複合㈣之囉，添加对 磨耗顆粒如从〇3、sic、wc、⑽之铭基複合材料受到廣 泛的重視與研究’開發出許多具有耐磨耗之錢基複合材 料。 中華民國專利號碼300253之「鋁基複合材料製造方 去」，係將金屬熔湯置於含氧氣氛下攪拌，使部份金屬熔 ，氧化形成細密之氧化物，均勻分佈於未被氧化之金屬熔 嘢内之製造方法。另外中華民國專利號碼1300010之「顆粒 刀政方法及设備」，係提供一種將強化顆粒及介面活性劑 攪拌後，經超音波震盪使顆粒分散再加入熔湯内之製造方 法。此外中華民國專利號碼1992〇4之「次微米顆粒鋁基複 合材料製造方法」，係利用固體旋轉摩擦製得含氧化鋁顆 粒與鋁結合之磨屑後，再置入鋁熔湯機械攪拌混合的方 去。先刚提及之專利都具有強化粒子在金屬基材中之分佈不 201224168 均勻與澆鑄凝固過慢形成偏析等問題。 “。以上所述’現有!g基複合材料製造方法繁多，在設 計與，作上也不盡相同，因此在預期的效果也不盡相同。 如何付到種成本低、高磨耗及運輸結構組件之應用，乃 為目前複合材料業者祕解決之重要技術問題。 【發明内容】 本發明係提供-種祕複合⑽製作方法，主要是解決 強化粒子在金屬基材巾之分佈柯自與鱗凝㈣慢形成偏 析之問題。 本發明主要是將高純度Mg、⑷、Si及&等材料，在 一炼解爐中進煉，⑽後經除氣、除料處理後，再將 溶融金m-電簡m與添加—強化粒子（如 2f3 SiC、WC及BN等材料)進行充分攪拌混合，以激冷 洗鑄方式製成擠旋，驗經一均質化溫度(如衫叱至5贼) 處理後’於一加工溫度(如叱至彻。cm齊製(如擠製比為 4〇.1至90:1)或軋延(軋延率為·至9〇⑴製成板材。藉此 種方法解Λ則b粒子在金屬基材分佈不均勾錢鑄凝固過 慢形成偏析等問題》 進—步，軋延板材經固溶處理淬火溫度(如5〇〇它至55〇 °〇進行©溶處料火，再㈣人王報溫度(如15叱至 2〇〇c)進行析出處理〇.5小時至10辦後，藉此種方法可 獲得—高抗拉強度及高剛性之材料。 關於本發明之優點與精神可以藉由以下的創作詳述及所 201224168 附圖式得到進一步的瞭解。 【實施方式】 請參見圖一，圖一係繪示根據本發明之一具體實施例 之絲複合材料製作方法。如圖所示，首先，執行步驟S10， 主要將高純度Mg、A1、si、Cu原料，在—熔解爐中(如高週 波感應熔解爐或電阻式加熱爐)進行熔解。201224168, invention description: [Technical field to which the invention belongs] Application material provides the age-based composite material (4) as a method, _ is about the analysis of the metal distribution at the metal level (4) sharp casting condensation 111 too slow to form a bias. , in order to achieve low cost, high wear, suitable for transporting structural components [prior art] In recent years, the application of metal-based composite materials with light weight, high rigidity, strength and thermal stability is resistant to use. The wheel of the wear component industry. In order to improve the metal matrix composite (4), the addition of wear particles such as 〇3, sic, wc, and (10) has attracted extensive attention and research to develop a number of wear-resistant money-based composite materials. The Republic of China Patent No. 300253 "Aluminum-based composite material manufacturing side" is to stir the molten metal in an oxygen-containing atmosphere to melt part of the metal, oxidize to form fine oxides, and evenly distribute the unoxidized metal. Manufacturing method in the melting pot. In addition, the "Pellet Knife Method and Equipment" of the Republic of China Patent No. 1,300,010 provides a manufacturing method in which the granules and the surfactant are stirred and then ultrasonically oscillated to disperse the particles and then add them to the melt. In addition, the method of manufacturing the sub-micron-particle aluminum-based composite material of the Republic of China Patent No. 1992〇4 is to use the solid rotary friction to obtain the abrasive grains containing the alumina particles combined with the aluminum, and then placed in the aluminum melting soup mechanically mixed and mixed. Go. The patents just mentioned have the problem that the distribution of the reinforcing particles in the metal substrate is not 201224168. The uniformity and the solidification of the casting are too slow to form segregation. "The above-mentioned 'existing! g-based composite materials manufacturing methods are numerous, and they are not the same in design and operation, so the expected effects are not the same. How to pay for low cost, high wear and transportation structural components The application is an important technical problem solved by the composite material industry. [Invention] The present invention provides a method for making a secret compound (10), which mainly solves the distribution of the reinforcing particles in the metal substrate towel. The problem of slowly forming segregation. The invention mainly comprises high-purity Mg, (4), Si and & materials in a refining furnace, (10) after degassing and material removal treatment, and then melting gold m- The electric simple m and the added-enhanced particles (such as 2f3 SiC, WC and BN materials) are thoroughly stirred and mixed, and the squeezing is performed by chilling and washing, and the homogenization temperature (such as the sputum to 5 thief) is treated. After the 'processing temperature (such as 叱 彻 。 cm cm cm cm cm cm cm cm cm cm cm ( ( ( cm cm cm cm cm 或 或 或 或 或 或 或 或 或 或 或 或 或 或 或 或 或 或 或 或 或 或 或The method solves the problem that the b particles are unevenly distributed on the metal substrate, and the solidification of the particles is too slow to form segregation. Problem: Step-by-step, rolling the sheet through the solution treatment quenching temperature (such as 5 〇〇 to 55 ° ° 〇 for the dissolution of the material fire, and then (4) Ren Wang reported the temperature (such as 15 叱 to 2 〇〇 c) The precipitation treatment can be obtained after 5 hours to 10, and the material with high tensile strength and high rigidity can be obtained by the method. The advantages and spirit of the present invention can be obtained by the following detailed description and the 201224168 drawing. [Embodiment] Referring to Figure 1, Figure 1 shows a method for fabricating a silk composite material according to an embodiment of the present invention. As shown in the figure, first, step S10 is performed, mainly for high-purity Mg, The A1, Si, and Cu raw materials are melted in a melting furnace such as a high frequency induction melting furnace or a resistance heating furnace.
接著，執行步驟S11,經除氣、除渣等方式處理後，熔融 金屬體注人-電_拌_，與—添加AlA触粒子充分搜 拌混合，再以激冷澆鑄(DC)成直徑203.2mm長度約Im的鑄 錠’其成份分別為6061/1〇 wt% MO3、6〇61/15加％ αιλ及 6061/20 wt/〇 八丨2〇3 ’ 其金相組織（Ke丨ier’s reagent, χ 1⑻）如 圖至一所示，顯不八丨2〇3強化粒子分佈均勻且無偏析現象。 最後，執行步驟S12 ,擠棒經均質化溫度(如53(rc)處理 =’於加工溫度在350°C下擠製成厚6mm寬i〇0mm之板材，擠 製比約為60:1 ’其金相組織如圖四至六所示（Keller，s reagent， χ 100) ’ 顯示6061/10 wt% Al2〇3、6061/15 加％ A]2〇3、及 6061/20 wt% Al2〇3擠製材晶粒尺寸均約25_且处〇3強化粒 子分佈均勻且無偏析現象。 更進一步’執行S13，擠製材再於加工溫度下及80%之 乾延率下’軋延成U麵厚度之薄板材。再經T6處理(在 53〇c進仃m溶處辦火，躲175〇c進行8小時人工時效處 理），其金相組織（KeUer，sreagent，x _如圖七至九所示， 顯示為晶粒尺寸由擠製時25/zm細化至如m，且Al2〇3強 化粒子破碎分佈更為均勻。 201224168 以擠製材、80%軋延材、及80%軋延後T6處理材的常溫 拉伸之機械性質比較，如表一所示。 表一 試樣 6061 6061/10 wt% Ah〇3 6061/15 wt% AI2O3 6061/20 wt% AI2O3 機械 性質 ---- 抗袓強 度 (MPa) 楊氏模數 (GPa) 抗拉強 度(MPa) 楊氏模 數 (GPa) 抗拉強 度(MPa) 楊氏模 數 (GPa) 抗拉強 度(MPa) 揚氏模數 (GPa) 擠製 材 124 --- 145 — 160 —— 166 — 80%軋 延材 *· ·· · — 260 —— 265 — 280 — 80%軋 延-T6 處理 材 310 70 372 90 385 102 390 110 本發明係提供一種鋁基複合材料製作方法，擠製材在室 溫下的抗拉強度為145至166 MPa，較一般未添加強化粒子(如 A1203)的6061之抗拉強度124 MPa，其抗拉強度提高約20至45 MPa左右，但再經常溫下軋延製成6061/10 wt% A1203、 6061/15 wt% Al2〇3、及6061/20 wt% Al2〇3板材，其抗拉強度 分別為260、265及280 MPa，其抗拉強度提高約110 MPa左 右。 更進一步，6061、6061/10 wt% Al2〇3、6061/15 wt% 201224168 ΑΙΛ、及6061/20 wt% ΑΙΛ板材經由丁6處理後之抗拉強度 可分別為372、385及390 MPa ;揚氏模數則分別為9〇、1〇2^ 110 GPa ’較一般未添加強化粒子(如A12〇3)_〇61板材且經過 T6處理後之抗拉強度為310 MPa ;楊氏模數為7〇，其抗拉強 度和楊氏模數分別提高約60至80 MPa和20至40 GPa，添加強 化粒子且進過T6處理後之抗拉強度及剛性均有明顯性提高。 另針對6061/10 wt% ΑΙΑ、6061/15 wt% Al2〇3、6〇61/2〇 wt%Then, step S11 is performed, after the process of degassing, slag removal, etc., the molten metal body is injected into the electric-electric_mixing_, and the AlA contact particles are fully mixed and mixed, and then chilled and cast (DC) into a diameter of 203.2. Ingots with a mm length of about Im' have a composition of 6061/1〇wt% MO3, 6〇61/15 plus % αιλ and 6061/20 wt/〇八丨2〇3 ' of their metallographic structure (Ke丨ier's reagent) , χ 1 (8)) As shown in the figure to the first, it is obvious that the entangled particles are evenly distributed and have no segregation. Finally, step S12 is performed, and the extruded rod is subjected to a homogenization temperature (for example, 53(rc) treatment=', and the processing temperature is extruded at 350 ° C to form a sheet having a thickness of 6 mm and a width of 0 mm, and the extrusion ratio is about 60:1 ' The metallographic structure is shown in Figures 4-6 (Keller, s reagent, χ 100) ' shows 6061/10 wt% Al2〇3, 6061/15 plus % A]2〇3, and 6061/20 wt% Al2〇3 The grain size of the extruded material is about 25 _ and the distribution of the reinforced particles at the 〇3 is uniform and there is no segregation. Further, 'Execution S13, the extruded material is then rolled to the U-face thickness at the processing temperature and 80% dry elongation. Thin sheet. After T6 treatment (fire at 53〇c into the solution, 175〇c for 8 hours artificial aging treatment), its metallographic organization (KeUer, sreagent, x _ as shown in Figures 7 to 9 It is shown that the grain size is refined from 25/zm at the time of extrusion to m, and the Al2〇3 strengthened particle crushing distribution is more uniform. 201224168 Extrusion, 80% rolled, and 80% post-rolling T6 The mechanical properties of the treated material at room temperature stretching are shown in Table 1. Table 1 Sample 6061 6061/10 wt% Ah〇3 6061/15 wt% AI2O3 6061/20 wt% AI2O3 Mechanical Properties---- Strength (MPa) Young's modulus (GPa) Tensile strength (MPa) Young's modulus (GPa) Tensile strength (MPa) Young's modulus (GPa) Tensile strength (MPa) Young's modulus (GPa) Extruded material 124 --- 145 — 160 — 166 — 80% rolled material*··· · — 260 —— 265 — 280 — 80% rolling-T6 processing material 310 70 372 90 385 102 390 110 The invention provides a method for preparing an aluminum-based composite material, wherein the tensile strength of the extruded material is 145 to 166 MPa at room temperature, and the tensile strength of the 6061 is generally increased by 124 MPa, and the tensile strength is improved by about 6.4 MPa, which is generally not added with reinforcing particles (such as A1203). 20 to 45 MPa, but often rolled down to make 6061/10 wt% A1203, 6061/15 wt% Al2〇3, and 6061/20 wt% Al2〇3 sheet, the tensile strength is 260, respectively. 265 and 280 MPa, the tensile strength is increased by about 110 MPa. Further, 6061, 6061/10 wt% Al2〇3, 6061/15 wt% 201224168 ΑΙΛ, and 6061/20 wt% ΑΙΛ plate after treatment with D6 The tensile strengths are 372, 385 and 390 MPa, respectively, and the Young's modulus is 9 〇, 1 〇 2^ 110 GPa respectively. Generally, no strengthening particles are added (such as A12 〇 3) _ The tensile strength of the 61 sheet and treated with T6 is 310 MPa; the Young's modulus is 7 〇, and its tensile strength and Young's modulus are increased by about 60 to 80 MPa and 20 to 40 GPa, respectively, and reinforcing particles are added. The tensile strength and rigidity after T6 treatment are significantly improved. Also for 6061/10 wt% ΑΙΑ, 6061/15 wt% Al2〇3, 6〇61/2〇 wt%
Al2〇3完成之板材作磨耗實驗，其結果以荷重35N鋼球測試常 溫磨耗速率均低於，此鋁基複合材料具備有 尚抗拉強度、高剛性及高耐磨性，可廣泛運用為汽車、家電 及0A等產業產品耐磨耗之結構件。 上述之實施例僅為例示性說明本發明之特點及其功 效，而非用於限制本發明之實質技術内容的範圍。任何熟 習此技藝之人士均可在不違背本發明之精神及範疇下，對 上111貫施例進行修娜與變化。因此，本發明之權利保護範 圍，應如後述之申請專利範圍所列。 【圖式簡單說明】 圖一係根據本發明之—具體實施例之鋁基複合材料製作方 法。 圖二係根據本發明之一具體實施中該6061/10 wt% A1203的金 相組織。 圖二係根據本發明之一具體實施中該6061/15 wt%八1203的金 相組織。 201224168 圖四係根據本發明之一具體實施中該6061/20 wt% A1203的金 相組織。 圖五係根據本發明之一具體實施中該6061/10 wt% A1203擠製 材的金相組織。 圖六係根據本發明之一具體實施中該6061/15 wt% Al2〇3擠製 材的金相組織。 圖七係根據本發明之一具體實施中該6061/20 wt% Al2〇3擠製 材的金相組織。 圖八係根據本發明之一具體實施中該6061/1() wt〇/〇 Al2〇3 80%軋延經T6處理材的金相組織。 圖九係根據本發明之一具體實施中該6061/15 wt% αι2ο3 80%軋延經Τ6處理材的金相組織。 圖十係根據本發明之一具體實施中該6〇61/2〇 Α12〇3 80%軋延經Τ6處理材的金相組織。 【主要元件符號說明】The wear test of the plate finished with Al2〇3 results in the wear rate of the normal temperature of the 35N steel ball test being lower than that. The aluminum matrix composite material has the tensile strength, high rigidity and high wear resistance, and can be widely used as a car. Structural parts for wear resistance of industrial products such as home appliances and 0A. The above-described embodiments are merely illustrative of the features and advantages of the present invention and are not intended to limit the scope of the invention. Anyone skilled in the art can practice and change the above 111 examples without departing from the spirit and scope of the invention. Therefore, the scope of protection of the present invention should be as set forth in the appended claims. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a view showing a method of producing an aluminum-based composite material according to a specific embodiment of the present invention. Figure 2 is a metallographic structure of the 6061/10 wt% A1203 in accordance with one embodiment of the present invention. Figure 2 is a metallographic structure of the 6061/15 wt% eight 1203 in accordance with one embodiment of the present invention. 201224168 Figure 4 is a metallographic structure of the 6061/20 wt% A1203 in accordance with one embodiment of the present invention. Figure 5 is a metallographic structure of the 6061/10 wt% A1203 extruded material in accordance with one embodiment of the present invention. Figure 6 is a metallographic structure of the 6061/15 wt% Al2〇3 extruded material in accordance with one embodiment of the present invention. Figure 7 is a metallographic structure of the 6061/20 wt% Al2〇3 extruded material in accordance with one embodiment of the present invention. Figure 8 is a metallographic structure of the 606/1() wt〇/〇 Al2〇3 80% rolled T6 treated material according to one embodiment of the present invention. Figure 9 is a metallographic structure of the 6061/15 wt% αι2ο3 80% rolled Τ6 treated material according to one embodiment of the present invention. Figure 10 is a metallographic structure of the 6〇61/2〇 Α12〇3 80% rolled Τ6 treated material according to one embodiment of the present invention. [Main component symbol description]