200925292 九、發明說明： 【發明所屬之技術領域】 本發明是有關於一種鋁合金之製造方法，特別是指— 種尚強度與高成型性铭合金之製造方法。 【先前技術】 紹合金具有優良之高熱傳導性、加工成型性、耐姓性 與表面光澤性等優點，故被廣泛地應用於食品包裝、家電 、建築與運輸等民生工業上，在日常生活中，小至電=器 、瓶蓋片，大至船舶、汽車等皆可見其蹤影存在。近年來 ，隨著高科技電子產業的蓬勃發展，鋁合金正以其優良之 散熱、導電、質輕、防磁遮蔽等性能，逐步跨入各式3C電 子零組件領域，尤以3C產品的成長最為明顯，而3c產品 之外觀殼件對於材料機械性能、成型性、彎曲性與表面品 質之要求特別嚴苛，目前一般3C電子零組件所使用的鋁材 以傳統之5052-H32材料為主（Al-Mg-Cr合金），主要是基於 鎂（Mg)元素具有固溶強化與加工硬化之雙重特性，且添加 鉻（Cr)元素具有細化晶粒、提高再結晶溫度與改善耐應力腐 餘性之功效。 但疋’由於鉻元素的添加極易產生Al7Cr之巨大晶出物 ’因而降低材料的破壞勃性與陽極處理性能，且隨著材料 薄片化與降低成本之需求，傳統5052合金已漸無法滿足強 度與形狀複雜之成型性能需求（彎曲成型較易破裂），再者， 傳統5052合金在製造上需經過原料溶解、鋁合金胚料製備 、熱軋預熱、熱軋延、冷軋延、t間退火攝氏32〇度）、冷 5 200925292 乾延05〜2〇%冷軋量）、安定化熱處理（攝氏180度）等繁複步 驟，造成鋁片成品因生產製程過長而導致表面產生鑿痕、 ’油焦的缺陷’相當不利於現今在3C產業中逐漸提高的表面 °°桌要求，因此，習知的鋁合金製造方法上仍有許多可進 步的空間。 【發明内容】 因此，本發明之目的，即在提供一種可有效縮短生產 製程’且成品具有高強度與高成型性之機械特性的鋁合金 _© 製造方法。 於是’本發明之高強度與高成型性鋁合金之製造方法 ，包含一備料步驟、一澆鑄成型步驟、一熱軋延預熱步驟 熱軋延步驟、一冷軋延步驟，及一退火步驟。 該備料步驟是將重量百分比〇.15wt%〜0_25wt%的鐵、重 量百分比〇.25wt%〜〇.75wt%的猛，重量百分比在 2.4wt%〜3.4wt%的鎂，及重量百分比在〇2〇wt%以下的矽熔 ❹ 融於平衡量之鋁原料中，以備製出一熔融狀態之鋁合金原 料’其中’該鋁原料含有無法避免且重量百分比在〇 lwt〇/〇 以下的雜質。 該洗鑄成型步驟是將熔融之該鋁合金原料經過澆鑄而 成型一鋁胚料。 該熱軋延預熱步驟是將成型後之鋁胚料置於一攝氏5〇〇 度以上之預熱爐内，並保持至少二小時以上。 δ亥熱軋延步驟是將經過該熱軋延預熱步驟後之鋁胚料 於攝氏350〜500〇C之間進行熱軋延並形成一鋁捲料。 6 200925292 • 該冷軋延步驟是將經過該熱軋延步驟後之鋁捲料待冷 部至室溫後再予以冷軋，且冷軋量是在60%以上。 该退火步驟是將經過該冷軋延步驟後之鋁捲料予以退 火熱處理，退火溫度是介於24〇°C〜270°C之間，退火時間是 至少2小時以上。 本發明之功效在於鋁合金的製造過程中，利用特定重 量γ分比的短元素來取代習知的鉻元素，使如習知般的巨 ❹ *日日A物不會產丨’同時達到細化晶粒及降低退火敏感性 之功效，另外，在生產製程方面也只需經過備料、澆鑄成 型、熱軋延預熱、熱軋延、冷軋延，及退火步驟就可完成 ，亦有縮短製程之功效，進而節省製造時間與成本。 【實施方式】 有關本發明之前述及其他技術内容、特點與功效，在 、下配口參考圖式之五個較佳實施例的詳細說明中，將可 清楚的呈現。 〇 在本發明被詳細描述之前，要注意的是，在以下的說 明中，類似的元件是以相同的編號來表示。 如圖1所示，本發明高強度與高成型性鋁合金之製造 方法的第一較佳實施例，包含一備料步驟11、一澆鑄成型 步驟12、一熱軋延預熱步驟13、一熱軋延步驟14、一冷軋 延步驟15，及一退火步驟16。 首先進行該備料步驟U，該備料步驟U是將重量百分 比〇.15wt%〜〇.25wt%的鐵、重量百分比為〇.25wt%的錳、重 ΐ百分比在2.4wt%的鎂，及重量百分比在〇 2〇wt%以下的 7 200925292 矽，熔融於平衡量之鋁原料中，以備製出一熔融狀態之鋁 ' 合金原料，其中，該鋁原料含有無法避免且重量百分比在 0.1 wt°/〇以下的雜質（如銅、欽、棚等元素）。 在本實施例中，該鎂元素的重量百分比是控制在 2.4wt%，另外，本實施例是使用錳元素來代替習知的鉻元 素，猛的添加重量百分比為0.25wt%，主要考量為猛元素之 添加不僅具有促進加工硬化、增加強度外，亦擁有細化晶 粒與降低退火敏感性之功效，有利於實際操作之生產，且 ® 由於其本身和Al、Fe等合金元素具有極高之親和力，因此 不論在澆鑄過程或預熱步驟中，均能發現含錳之晶出物 (Eutectic Precipitate)或二次析出物（2nd Precipitate)存在，此 類的晶出物或二次析出物是必要的，其可促使鋁材内形成 微細之次晶粒。但Μη添加量若低於0.25wt%，則其效果不 佳。 鐵元素添加方面，由於鐵元素能固溶於鋁材之量不多（ 最大固溶量僅〇.〇52wt%)，因此大部份之鐵原子便和其它合 ^ 金原子相結合，而以 Al-Fe-Mn相的晶出物（Eutectic200925292 IX. DESCRIPTION OF THE INVENTION: TECHNICAL FIELD The present invention relates to a method for producing an aluminum alloy, and more particularly to a method for producing a high strength and high moldability alloy. [Prior Art] Shao alloy has excellent high thermal conductivity, processing formability, resistance to surname and surface gloss, etc., so it is widely used in food packaging, home appliances, construction and transportation, etc. in daily life, in daily life. Small to electric = device, bottle caps, as large as ships, cars, etc. can be seen. In recent years, with the vigorous development of high-tech electronics industry, aluminum alloy is gradually entering the various 3C electronic components field with its excellent heat dissipation, conductivity, light weight, anti-magnetic shielding and other properties, especially the growth of 3C products. Obviously, the appearance of the 3c product shell is particularly demanding on the mechanical properties, formability, bendability and surface quality of the material. At present, the aluminum used in the general 3C electronic components is mainly based on the traditional 5052-H32 material (Al -Mg-Cr alloy), mainly based on the dual characteristics of solid solution strengthening and work hardening of magnesium (Mg) elements, and adding chromium (Cr) elements to refine grains, improve recrystallization temperature and improve stress and corrosion resistance The effect. However, 疋 'due to the addition of chromium element is very easy to produce large crystallites of Al7Cr', thus reducing the destructive properties of the material and the anodizing performance, and with the demand for material thinning and cost reduction, the traditional 5052 alloy has gradually failed to meet the strength. With the complex shape forming performance requirements (bending forming is easy to break), in addition, the traditional 5052 alloy needs to be processed by raw material dissolution, aluminum alloy billet preparation, hot rolling preheating, hot rolling, cold rolling, t Annealing 32 degrees Celsius), cold 5 200925292 dry extension 05~2〇% cold rolling amount, and stability heat treatment (180 degrees Celsius) and other complicated steps, resulting in aluminum sheet finished product due to excessive production process, resulting in surface chiseling, The 'defect of oil coke' is quite unfavorable for the surface table requirements that are gradually increasing in the 3C industry today. Therefore, there are still many room for improvement in the conventional aluminum alloy manufacturing method. SUMMARY OF THE INVENTION Accordingly, it is an object of the present invention to provide an aluminum alloy manufacturing method which can effectively shorten the production process and which has high mechanical strength and high formability. Thus, the method for producing a high-strength and high-formability aluminum alloy according to the present invention comprises a preparation step, a casting molding step, a hot rolling preheating step, a hot rolling step, a cold rolling step, and an annealing step. The preparation step is to add 5% by weight to 15% by weight to 0% by weight of iron, 5% by weight to 5% by weight, 5% by weight to 5% by weight of magnesium, and 5% by weight. The ruthenium melt of less than 〇wt% is melted into the balance of the aluminum raw material to prepare a molten aluminum alloy raw material, wherein the aluminum raw material contains impurities which are unavoidable and the weight percentage is less than 〇lwt〇/〇. The die-casting step is to mold the molten aluminum alloy material to form an aluminum billet. The hot rolling preheating step is to place the formed aluminum billet in a preheating furnace of more than 5 degrees Celsius for at least two hours. The δ hot rolling step is to hot-roll the aluminum billet after the hot rolling preheating step between 350 and 500 〇C to form an aluminum coil. 6 200925292 • The cold rolling step is to cold-roll the aluminum coil after the hot rolling step to be cooled to room temperature, and the cold rolling amount is 60% or more. The annealing step is to heat-treat the aluminum coil after the cold rolling step, the annealing temperature is between 24 ° C and 270 ° C, and the annealing time is at least 2 hours. The effect of the present invention is that in the manufacturing process of the aluminum alloy, the short element of a specific weight γ ratio is used to replace the conventional chrome element, so that the conventional cockroach can not be produced at the same time. The effect of crystallization and reducing the sensitivity of annealing. In addition, the production process can be completed only by stock preparation, casting, hot rolling, preheating, hot rolling, cold rolling, and annealing. The efficiency of the process, which in turn saves manufacturing time and costs. [Embodiment] The foregoing and other technical contents, features, and advantages of the present invention will be apparent from the detailed description of the preferred embodiments of the present invention. Before the present invention is described in detail, it is noted that in the following description, like elements are denoted by the same reference numerals. As shown in FIG. 1, a first preferred embodiment of the method for manufacturing a high strength and high formability aluminum alloy according to the present invention comprises a preparation step 11, a casting step 12, a hot rolling preheat step 13, and a heat. Rolling step 14, a cold rolling step 15, and an annealing step 16. First, the preparation step U is performed. The preparation step U is 5% by weight to 15% by weight of iron, 5% by weight of manganese, 5% by weight of magnesium, and percentage by weight of 2.4% by weight of magnesium. 7 200925292 〇 below 〇 2 〇 wt%, melted in an equilibrium amount of aluminum raw material to prepare a molten aluminum alloy material, wherein the aluminum raw material contains unavoidable weight percentage at 0.1 wt ° / 〇 The following impurities (such as copper, chin, shed, etc.). In this embodiment, the weight percentage of the magnesium element is controlled at 2.4% by weight. In addition, in this embodiment, manganese element is used instead of the conventional chromium element, and the weight percentage is 0.25 wt%, mainly considering The addition of elements not only promotes work hardening and increases strength, but also has the effect of refining grains and reducing annealing sensitivity, which is beneficial to practical production, and is extremely high due to its own alloying elements such as Al and Fe. Affinity, therefore, whether in the casting process or in the preheating step, the presence of manganese-containing crystals (Eutectic Precipitate) or secondary precipitates (2nd Precipitate) can be found. Such crystallites or secondary precipitates are necessary. It can promote the formation of fine secondary grains in the aluminum material. However, if the amount of Μη added is less than 0.25 wt%, the effect is not good. In terms of iron addition, since iron is soluble in aluminum in a small amount (the maximum solid solution is only 〇.〇52wt%), most of the iron atoms are combined with other gold atoms. Crystalline of Al-Fe-Mn phase (Eutectic
Precipitate)或二次析出物（2nd Precipitate)存在，但過量鐵元 素的添加，於澆鑄過程中即易形成巨大之晶出物，此類晶 出物因為硬度高且與鋁材之結合性不良，故往往也是成型 加工過程中，鋁片破裂之起源。因此鐵合金的添加範圍以 0.15 〜0.25 wt% 為宜。 矽合金的添加方面，矽合金所扮演之角色較為特殊， 一般在純鋁錠中即含有約0.20%wt以下之矽合金，當矽以 8 200925292 原子狀態固溶或以純元素方式析出，對鋁合金之物性影響 不如以化口物方式析出明顯。因此少量矽合金添加並不影 響其性尨’但過量之矽添加，在不適當之製程中，極易在 退火熱處理後導致再結晶晶粒粗化，在加工成型過程中， ;紹材表面t/成橘皮效應（Qrange Pal)。因此⑦合金的添加 範圍以0.20wt以下為宜。 接著進行該澆鑄成型步驟12，該澆鑄成型步驟12是 將溶融之㈣合金原料經過濟鑄而成型出—銘胚料，由於 澆鑄用之鑄模及方法皆為業界習知的技術，在此則不對其 進一步說明。 ^ 之後，進行該熱軋延預熱步驟13，該熱軋延預熱步驟 13是將成型後之銘胚料置於-攝氏，度以上之預熱爐内 並保持至v 一小扦以上。在本步驟中，該鋁胚料被加熱 以利後續之熱軋延製程，而該鋁胚料同時也會藉由該預熱 爐内之高溫而均質化，即預熱兼均質化之功效，銘胚料均 質化的目的主要是消除澆鑄過程中Mg元素之逆偏析，以縮 小各項材質性㈣變異性，若預熱溫度低於則。C或是預熱 時間J於2小時，則其均質化效果不佳，進而失去其消除 Mg逆偏析之效果。 然後，進行該熱軋延步驟14，該熱札延步驟14是將經 過該熱軋延預熱步驟13後之鋁胚料於攝氏35〇〜5〇〇間進行 熱軋延’而經過此熱軋延步驟14後之銘胚料即會成片狀， 並盤捲成為鋁捲料。 接著，進行該冷軋延步驟15，該冷軋延步驟15是將經 9 200925292 過健軋延步驟14後之㈣料，待冷卻至室溫後再予以冷 =且冷#L量是在60%以上。而在冷軋延過程中，上述備 製步驟1中所添加的鐵、料元素便會阻礙冷加工差排 (DlSl〇Catl〇n)的移動，讓差排於該銘捲料内迅速累積，藉此 達到提高軸捲料之抗拉強度的目的，即是所謂的冷^強 化（Coldw〇rkstrengthening)現象，若冷乾量在以下時， 則其機械強度將不足。另外要注意的是，在該熱乳延步驟 癱 Η及冷乳延步驟15中所用之軋延機皆為業界現有之設備， ® 應為對此㈣領域有通常知制人職悉，所以在 以 贅述。 最後，進行該退火㈣16 ’料火步驟16是將經過該 冷軋延步驟15後之|s捲料予以退火熱處理，退火溫度是介 :240t〜270。〇之間，且退火時間是至少2小時以上：藉由 μ退火仙’使原先被㈣的冷加卫差排能夠部分脫離固 溶元素（鐵、猛）的牵綷而移動，使該銘捲料内部微觀組織之 錢能獲得更佳的排列，以提高該㈣料之延展性。 本發明高強度與高成型性鋁合金之製造方法之第二較 佳實施例，大致上^與該第-較佳實施例相同，相同之處不 再贅s，其中不相同之處在於：在該備料步驟U中，鐵的 重量百分比為〇.15wt°/。〜〇.25wt%，鍾的重量百分比為 〇.75wt%’鎂的重量百分比纟2細％，矽的重量百：比為 〇.2〇Wt%;但是要注意的是，在錳元素的添加上必需符合 (%Mn)<0.805之限制，上述之目的是以不因添加鐘元素而造 成巨大晶出物（Al-Fe-Mn相）為考量。 10 200925292 本發明高強度與高成型性鋁合金之製造方法之第三較 • 佳實施例，大致上是與該第一較佳實施例相同，相同之處 不再贅言，其中不相同之處在於：在該備料步驟11中’鐵 的重量百分比為〇.15wt%~0.25wt% ’猛的重量百分比為 0.25wt%，鎂的重量百分比在3.4wt%，矽的重量百分比為 0.20wt%，其中Mg若添加過量則在成型加工階段時，工作 物之表面極易產生伸張應變痕（Stretch strain mark)缺陷，因 此Mg添加量設定以不超過3.4wt%為宜。 © 本發明高強度與高成型性鋁合金之製造方法之第四較 佳實施例，大致上是與該第一較佳實施例相同，相同之處不 再贅言，其中不相同之處在於：在該備料步驟11中，鐵的 重量百分比為 〇.15wt%〜0.25wt%，锰的重量百分比為 0.75wt%，鎂的重量百分比在3.4wt%，矽的重量百分比為 0_20wt%。 經過實驗證明，利用上述之四個實施例所揭露的製造 方法所製出的鋁合金，可藉由參閱下列表一看出其特性及與 習知的比較，表一中之艾氏值（Erichsen value)係雙轴向之 伸展能力的測試值，其值越高即表示成型性能越佳。 表一 材質 抗拉強度 (MPa) 延伸率 (%) 艾氏值 (mm) 彎曲性 (180 度，〇t) 5052-H32 (習知） 227 14 6.0 差 Al-2.4%Mg-0.25%Mn(實施例 1) 233 17 7.5 優 Al-2.4%Mg-0.75%Mn(實施例 2) 245 17 7.4 優 11 200925292 ---^-----I 便 由表一中可輕易看出，利用本發明所揭露的鋁合金製造 方法所製出之鋁合金，不論在抗拉強度、延伸率、艾氏值 ’及彎曲性等機械與成型性能上皆較習知的鋁合金要優良 再者，本發明主要藉由各種合金添加的效應產生密集的 二次析出物，此二次析出物在該退火步驟16時，亦具有抑 制次晶粒成長之效應（pinning效應）。Precipitate or secondary precipitates (2nd Precipitate), but the addition of excessive iron elements is likely to form huge crystals during the casting process. Such crystals are high in hardness and poorly bonded to aluminum. Therefore, it is often the origin of the fracture of the aluminum sheet during the molding process. Therefore, the addition range of the iron alloy is preferably 0.15 to 0.25 wt%. In the addition of niobium alloys, niobium alloys play a special role. Generally, they contain about 0.20% by weight of niobium alloy in pure aluminum ingots. When niobium is dissolved in 8 200925292 atomic state or precipitated as pure element, aluminum alloy The influence of physical properties is not as obvious as that of chemical substances. Therefore, the addition of a small amount of niobium alloy does not affect its properties, but the addition of niobium is excessive. In an inappropriate process, it is easy to cause recrystallization grain refining after annealing and heat treatment. / into the orange peel effect (Qrange Pal). Therefore, the addition range of the 7 alloy is preferably 0.20 wt or less. Then, the casting molding step 12 is carried out. The casting molding step 12 is to mold the molten (tetra) alloy raw material to form a billet, and since the casting mold and the method are all known in the industry, it is not correct here. It is further explained. After that, the hot rolling preheating step 13 is carried out, and the hot rolling preheating step 13 is performed by placing the formed billet in a preheating furnace of -Celsius or more and maintaining it for more than one hour. In this step, the aluminum billet is heated to facilitate the subsequent hot rolling process, and the aluminum billet is also homogenized by the high temperature in the preheating furnace, that is, the effect of preheating and homogenizing. The purpose of the homogenization of the blank is mainly to eliminate the reverse segregation of Mg elements in the casting process, so as to reduce the variability of each material (four), if the preheating temperature is lower. When C or the preheating time J is 2 hours, the homogenization effect is not good, and the effect of eliminating the reverse segregation of Mg is lost. Then, the hot rolling step 14 is performed. The heat drawing step 14 is to heat-roll the aluminum billet after the hot rolling step preheating step 13 between 35 〇 5 摄 而 and pass the heat. After the rolling step 14, the original billet is formed into a sheet and coiled into an aluminum coil. Next, the cold rolling step 15 is performed, and the cold rolling step 15 is to pass the (4) material after the step 14 of the 2009 200929 292. After cooling to room temperature, it is cooled and the amount of cold #L is 60. %the above. In the cold rolling process, the iron and material elements added in the preparation step 1 hinder the movement of the cold working differential row (DlSl〇Catl〇n), so that the difference is quickly accumulated in the inscription material. This achieves the purpose of increasing the tensile strength of the shaft coil, that is, the so-called cold-wound strengthening phenomenon, and if the amount of cold-drying is below, the mechanical strength will be insufficient. It should also be noted that the calenders used in the hot emulsion step and the cold emulsion step 15 are all existing equipment in the industry, and ® should have a general knowledge of the field in this (4) field, so To repeat. Finally, the annealing is performed. (4) The 16' firing step 16 is an annealing heat treatment of the |s coil after the cold rolling step 15, and the annealing temperature is 240t~270. Between the crucibles, and the annealing time is at least 2 hours or more: by μ annealing the immortalization of the original (four) cold-added differential row can be partially removed from the solid solution element (iron, fierce), so that the inscription It is expected that the money of the internal microstructure can be better aligned to improve the ductility of the material. The second preferred embodiment of the method for manufacturing a high-strength and high-formability aluminum alloy according to the present invention is substantially the same as the first preferred embodiment, and the same is no longer the same, wherein the difference is: In the preparation step U, the weight percentage of iron is 〇.15wt°/. ~ 〇.25wt%, the weight percentage of the clock is 〇.75wt% 'the weight percentage of magnesium 纟 2% by weight, the weight of 矽 is 100: the ratio is 〇.2〇Wt%; but it should be noted that the addition of manganese element It is necessary to comply with the limitation of (%Mn) < 0.805, and the above purpose is to consider the large crystallite (Al-Fe-Mn phase) which is not caused by the addition of the clock element. 10 200925292 The third preferred embodiment of the method for manufacturing a high-strength and high-formability aluminum alloy according to the present invention is substantially the same as the first preferred embodiment, and the similarities are no longer in common, wherein the difference is that : In the preparation step 11, 'the weight percentage of iron is 15.15wt%~0.25wt%', the weight percentage is 0.25wt%, the weight percentage of magnesium is 3.4wt%, and the weight percentage of bismuth is 0.20wt%, wherein If the Mg is excessively added, the surface of the workpiece is liable to cause a stretch strain mark defect at the molding processing stage, so that the Mg addition amount is preferably not more than 3.4% by weight. The fourth preferred embodiment of the method for manufacturing a high-strength and high-formability aluminum alloy according to the present invention is substantially the same as the first preferred embodiment, and the same is no longer in common, wherein the difference is that: In the preparation step 11, the weight percentage of iron is 1515 wt% to 0.25 wt%, the weight percentage of manganese is 0.75 wt%, the weight percentage of magnesium is 3.4 wt%, and the weight percentage of bismuth is 0-20 wt%. It has been experimentally proved that the aluminum alloy produced by the manufacturing method disclosed in the above four embodiments can be seen by referring to the following Table 1 and its comparison with the conventional ones, Eichsen in Table 1 (Erichsen Value) is the test value of the biaxial stretching ability. The higher the value, the better the molding performance. Table 1 Material Tensile Strength (MPa) Elongation (%) Ehrlich Value (mm) Flexibility (180 degrees, 〇t) 5052-H32 (conventional) 227 14 6.0 Poor Al-2.4% Mg-0.25% Mn ( Example 1) 233 17 7.5 Excellent Al-2.4% Mg-0.75% Mn (Example 2) 245 17 7.4 Excellent 11 200925292 ---^-----I can be easily seen from Table 1, using this The aluminum alloy produced by the aluminum alloy manufacturing method disclosed by the invention is superior to the conventional aluminum alloy in terms of mechanical strength and molding properties such as tensile strength, elongation, Ehrlich's value and bending property, and The invention mainly produces dense secondary precipitates by the effects of various alloy additions, and the secondary precipitates also have an effect of suppressing secondary grain growth (pinning effect) at the annealing step 16.
此外，本發明之鋁合金製造方法除了使成品兼具高強度 與高成型性能外，同時在製程上也較習知要縮短許多，進 而節省製作工時、複雜度以及所需耗費的成本，由於本發 明的生產製程較為流暢，約可比傳統生產製程（需42天）縮 短時間約14天。 如圖2所示，本發明高強度與高成型性鋁合金之製造方 法之第五較佳實施例，大致上是與該第一較佳實施例相同 ，相同之處不再贅言，其中不相同之處在於：當該澆鑄成 型步驟12完成後，是先經過一均質化步驟17後才進行該 熱軋延預熱步驟13，因此，該鋁胚料在成型後是先置於一 攝氏500度以上的均質化爐，且置於該均質化爐内至少二 小時以上’再將該銘胚料取出’並待該銘胚料冷卻至室溫 後再進行該熱軋延預熱步驟13，此時預熱時間則不需保持 二小時以上’該鋁胚料達到預熱溫度（攝氏5〇〇度）即可進行 熱軋延。此方式為預熱與均質化分別進行，除可充分運用 設備外’並可經由各項組合以減少生產排程的瓶頸。 12 200925292 歸納上述，本發明之南強度與南成型性铭合金之製造 方法，利用重量百分比在〇.25wt%〜〇.75wt%的錳元素來取代 習知的鉻/L素，使如習知般的巨大晶出物不會產出，同時達 到細化晶粒及降低退火敏感性之功效，另外，在生產製程方 面也只需經過備料、澆鑄成型、熱軋延預熱、熱軋延、冷軋 延，及退火等步驟就可製出比習知強度及成型性更佳的鋁合 金，同時兼具縮短製程之優點，進而節省製造時間與成本， 故確實能達到本發明之目的。 惟以上所述者，僅為本發明之較佳實施例而已，當不 能以此限定本發明實施之範圍，即大凡依本發明申請專利 範圍及發明说明内容所作之簡單的等效變化與修飾，皆仍 屬本發明專利涵蓋之範圍内。 【圖式簡單說明】 圖1疋一流程示意圖，說明本發明高強度與高成型性 鋁合金之製造方法的第一至第四較佳實施例；以及 圖2是一流程示意圖’說明本發明高強度與高成型性 鋁合金之製造方法的第五較佳實施例。 13 200925292 【主要元件符號說明】 11 ··· …備料步驟 15 ••…冷軋延步 12··· …澆鑄成型步驟 16···.· •…退火步驟 13··· …熱軋延預熱步驟 17.··· …·均質化步 14··. …熱軋延步驟In addition, the aluminum alloy manufacturing method of the present invention not only makes the finished product have high strength and high molding performance, but also has a much shorter process in the process, thereby saving manufacturing man-hours, complexity and cost. The production process of the invention is relatively smooth, and can be shortened by about 14 days compared with the conventional production process (42 days required). As shown in FIG. 2, the fifth preferred embodiment of the method for manufacturing the high-strength and high-formability aluminum alloy of the present invention is substantially the same as the first preferred embodiment, and the similarities are no longer in common, and are not the same. The hot rolling extension preheating step 13 is performed after the casting step 12 is completed. Therefore, the aluminum billet is first placed at a temperature of 500 degrees Celsius after molding. The above homogenization furnace is placed in the homogenization furnace for at least two hours or more, and then the raw material is taken out and the hot rolling delay preheating step 13 is performed after the billet is cooled to room temperature. When the preheating time is not required to be maintained for more than two hours, the aluminum billet can reach the preheating temperature (5 degrees Celsius) for hot rolling. This method is carried out separately for preheating and homogenization, except that the equipment can be fully utilized and can be combined to reduce the bottleneck of production scheduling. 12 200925292 In summary, the manufacturing method of the south strength and the south molding alloy of the present invention replaces the conventional chromium/L with a weight percentage of Mn.25wt%~〇.75wt% of the manganese element, so as to be known. The large crystal crystals will not be produced, and at the same time, the effect of refining the grains and reducing the sensitivity of annealing can be achieved. In addition, in the production process, only the preparation, casting, hot rolling, preheating, hot rolling, Cold rolling, annealing and other steps can produce aluminum alloys which are better than conventional strength and formability, and at the same time have the advantages of shortening the process, thereby saving manufacturing time and cost, and thus can achieve the object of the present invention. The above is only the preferred embodiment of the present invention, and the scope of the invention is not limited thereto, that is, the simple equivalent changes and modifications made by the scope of the invention and the description of the invention are All remain within the scope of the invention patent. BRIEF DESCRIPTION OF THE DRAWINGS FIG. 1 is a flow chart showing first to fourth preferred embodiments of a method for producing a high-strength and high-formability aluminum alloy according to the present invention; and FIG. 2 is a schematic flow diagram illustrating the present invention. A fifth preferred embodiment of a method of manufacturing a strength and high formability aluminum alloy. 13 200925292 [Description of main component symbols] 11 ··· ...Preparation step 15 ••...cold rolling step 12···...casting step 16······... annealing step 13···...hot rolling delay Thermal step 17.·····homogenization step 14··....hot rolling step
1414