200540280 九、發明說明： 【發明戶斤屬之技術領域】 發明領域 本發明係關於一種於高溫高速下具有優異成形性之鋁 5 -鎮合金板及其製造方法。 L先前技冬好]| 發明背景 铭-鎮合金質輕，強度及防蝕性優異，因此被提議用作 為汽車板材或其它加工材料或成形材料。但鋁_鎂合金於室 10溫之伸長率低，因此有鋁-鎂合金無法藉冷加工而成形為複 雜形狀的問題。因此理由故，基於鋁-鎂之超塑性合金可於 熱加工時抑制再結晶來縮小晶體之晶粒大小，以及於被展 延時可於例如500°C至550°C之高溫區獲得數百％伸長率， 因而可用於多項應用用途。 15 習知基於鋁-鎂之超塑性合金可於1 〇 ·4至1CT3 /秒之緩慢 成形速度(應變速率）顯示其超塑性，且需時長時間，因此當 應用於尋常加壓成形時生產力低且不合實際。 因此已經發展出即使使用高成形速度之應變速率例如 0.1/秒或以上，於熱加工之高溫區，換言之高於先前技術之 20 ι〇0倍或100倍以上，鋁合金板仍然可獲得足夠伸長率，因 此可抑制成形時的空腔出現。 例如日本專利申請公開案第1〇_259441號提出一種具 有於高速下之優異超塑性成形性以及於成形後具有較少量 工腔之IS合金板’其特徵在於其含有3.Q_8.〇%(wt%，後文 200540280 亦同）Mg、〇·21-〇.5〇% Cv^0.ooi-o.i% Ti含有Fe 0.06%或以 下及Si 0.06%或以下作為雜質以及差額為Ai及雜質，以及該 1呂合金板具有平均晶粒大小為20微米至200微米。 但先前技術，為了於最終所得板狀製品達成良好高溫 5高速成形性，有需要通過多項加工處理之問題，該等加工 處理諸如藉半連續澆鑄製造大型扁塊、表面剝皮、浸泡、 熱礼、冷軋、中間退火、最終軋製及最終退火，因而造成 板材製品之成本增高。 此外，大型扁塊於澆鑄時具有緩慢冷卻速度例如約i 10至1〇C/秒左右，因此中間化合物A1_Fe Si、Al6Mn等變粗 大’晶粒大小為數十微米或以上。即使於浸泡、熱軋、冷 軋、退火等最終板材製品，仍然維持1〇微米或以上之粗大 中間化合物。於高温成形時，於金屬間化合物與基體間之 父"面因剝皮而容易出現空腔。對於空腔之對治之道，採 用抑制鐵及石夕之含量至〇·1%或以下，但須使用昂貴之高純 度金屬來達成此項目的，因而有終產物之成本增高問題。 【發明内容】 發明概要 一本發明之目的係提供-種紹合金板，其可解決前述先 前技術之問題，而無需使用伴隨較高成本之高純度金屬， 可改良於高溫高速下之成形性，以及可減少成形後之空腔 ，以及提供一種該鋁合金板之製造方法。 為了達成前述目的，根據本發明，提供一種於高溫及 南速下具有優異成形性且於成形後之空腔數量減少之銘合 6 200540280 金板，其特徵在於該鋁合金板之組成為：200540280 IX. Description of the invention: [Technical field of the inventors] Field of the invention The present invention relates to an aluminum 5-ball alloy plate having excellent formability at high temperature and high speed, and a method for manufacturing the same. [L previous technology is good for winter] | Background of the Invention Ming-zheng alloys are light in weight, excellent in strength and corrosion resistance, and are therefore proposed to be used as automotive sheet materials or other processed materials or forming materials. However, the aluminum-magnesium alloy has a low elongation at room temperature, and therefore there is a problem that the aluminum-magnesium alloy cannot be formed into a complex shape by cold working. For this reason, aluminum-magnesium-based superplastic alloys can suppress recrystallization during thermal processing to reduce the crystal grain size, and can obtain hundreds of% in the high temperature region such as 500 ° C to 550 ° C during the spreading delay. Elongation, so it can be used for many applications. 15 It is known that aluminum-magnesium-based superplastic alloys can show their superplasticity at a slow forming speed (strain rate) of 10.4 to 1CT3 / second, and it takes a long time, so the productivity when applied to ordinary pressure forming Low and impractical. Therefore, it has been developed that the aluminum alloy plate can still obtain sufficient elongation even when using a strain rate of high forming speed such as 0.1 / second or more in the high temperature region of hot processing, in other words, 200 times or 100 times higher than the prior art. Ratio, so that the occurrence of cavities during molding can be suppressed. For example, Japanese Patent Application Laid-open No. 10-259441 proposes an IS alloy plate having excellent superplastic formability at high speed and a small number of cavities after forming, which is characterized in that it contains 3.Q_8.〇% (wt%, the same applies to the following 200540280) Mg, 0.21-0.50% Cv ^ 0.ooi-oi% Ti contains Fe 0.06% or less and Si 0.06% or less as impurities and the difference is Ai and impurities , And the 1 Lu alloy plate has an average grain size of 20 to 200 microns. However, in the prior art, in order to achieve good high-temperature and high-speed formability in the finally obtained plate-shaped products, there are problems that require multiple processing processes, such as semi-continuous casting to produce large flat pieces, surface peeling, soaking, and warming. , Cold rolling, intermediate annealing, final rolling and final annealing, thus causing the cost of sheet products to increase. In addition, the large slabs have a slow cooling rate during casting, for example, about 10 to 10 C / sec. Therefore, the intermediate compounds A1_Fe Si, Al6Mn, etc. become coarse ' Even in the final sheet products such as immersion, hot rolling, cold rolling, and annealing, the coarse intermediate compounds of 10 microns or more are still maintained. When forming at high temperature, the cavity between the intermetallic compound and the substrate is easy to appear due to peeling. For the countermeasure of the cavity, the content of iron and stone is suppressed to 0.1% or less, but expensive high-purity metals must be used to achieve this project, so the cost of the final product is increased. [Summary of the Invention] SUMMARY OF THE INVENTION An object of the present invention is to provide a seed-alloy alloy plate which can solve the aforementioned problems of the prior art, without using a high-purity metal accompanied by a higher cost, and can improve formability at high temperatures and speeds. And it can reduce the cavity after forming, and provide a method for manufacturing the aluminum alloy plate. In order to achieve the foregoing object, according to the present invention, an inscription 6 200540280 gold plate having excellent formability at high temperature and south speed and reduced number of cavities after forming is provided, which is characterized in that the composition of the aluminum alloy plate is:
Mg · 2.0-8.0 wt% ?Mg2.0-8.0 wt%?
Si : 0.06-0.2 wt%，Si: 0.06-0.2 wt%,
Fe : 0.1-0.5 wt%， 5 Μη : 0.1-0.5 wt%，以及 差額為鋁及無法避免的雜質，其中 具有當量圓直徑1微米至5微米之金屬間化合物之密度 為5000/平方毫米或以上，以及具有平均晶粒大小為20微米 或以下。 10 為了達成前述目的，根據本發明，進一步提供一種製 造一種於高溫及高速下具有優異成形性且於成形後之空腔 數量減少之本發明之鋁合金板，其特徵在於該製造方法包 含下列步驟： 製備一種具有本發明之鋁合金板組成之合金熔體， 15 藉雙帶澆鑄機，以冷卻速率20°C至150°C/秒，於澆鑄 期間於扁塊厚度之1/4位置澆鑄該合金熔體，來形成具有厚 度為5毫米至15毫米之扁塊， 隨後將該扁塊重新捲繞成為盤捲， 以冷軋減薄70%至96%冷軋由該盤捲所取得之扁塊， 20 以及 以5°C/秒或以上之溫度升高速率進行所得冷軋後合金 板之加熱退火至420°C至500°C。 本發明之鋁合金板界定化學組成範圍及顯微結構範圍 ，均勻且精密分散金屬間化合物，因此藉提高晶體晶粒細 200540280 度來改良於高溫高速下之成形性，而無需任何高純度金屬 ，以及可減少成形後之空腔。 —此外，本發明之製造方法藉雙帶錢，可於靖時獲 得高冷卻速率’限制冷軋減薄，限制冷乾後之退火條件， 5因而實現金屬間化合物之均句精密分散，以及提高晶體晶 粒之細度。 、、二由使用本發明之紹合金板，可獲得高級成形產品， • 成形時間縮短，且生產力提升。 【方包】 10較佳實施例之詳細說明 其=將說明限制本發明之合金之化學組成之理由。除 非另灯才曰不，否則於本說明書中表示化學組成之「％」表 示「Wt%」。 [Mg · 2·〇-8·〇%] 曰二、良強度之元素。為了表現此種效果，須將鎂含 • 量=定為2·〇%或以上。但若鎮含量超過8·0%，則薄扁塊之 =鑄低。如此鎖含量係限於2•⑽至8•⑽。若強調於洗 禱性’則較佳鎮含量進-步限於6·0%或以下。 [Si . 0.06-0.2%] 2〇 A1 p ^. 匕1為主、Mgji、及其它金屬間化合物之細 粒^又，石夕於冷乾後之退火時作為再結晶孕核產生位置之 功月匕。如此，此等金屬間化合物之粒子數目愈多，則產生 核數目愈多，結果形成之細小再結晶晶粒數目 4大此外’金相化合物之細擁子S3定所產生之再结 200540280 晶晶粒之晶粒邊界，由於晶體晶粒的合併而抑制成長，町 穩定維持細小再結晶晶粒。 為了發揮此等效果，需要讓矽含量為0 06%或以上。但 若矽含量超過〇·2%，則沉澱之金屬間化合物變粗大之趨勢 5變強，因而促成高溫變形時的空腔形成。如此，矽含量被 限於0·06%至0.2%。較佳範圍為〇 〇7%至〇 15%。 、通常，矽被視為雜質元素而欲以如同後述鐵之相同方 式去除，但於本發明，相反地存在有適量石夕，來提高如前 述再結晶晶粒之細度。如此無需高純度金屬，也未伴隨成 10 分的增高。 15Fe: 0.1-0.5 wt%, 5 Μη: 0.1-0.5 wt%, and the difference is aluminum and unavoidable impurities. Among them, the density of intermetallic compounds with equivalent circle diameters of 1 to 5 microns is 5000 / mm2 or more. , And has an average grain size of 20 microns or less. 10 In order to achieve the foregoing object, according to the present invention, there is further provided an aluminum alloy plate of the present invention that has excellent formability at high temperature and high speed and has a reduced number of cavities after forming, which is characterized in that the manufacturing method includes the following steps : Preparation of an alloy melt composed of the aluminum alloy plate of the present invention. 15 With a dual-belt casting machine, the cooling rate is 20 ° C to 150 ° C / second, and the casting is cast at a quarter of the thickness of the flat block during the casting. Alloy melt to form a flat block with a thickness of 5 mm to 15 mm, and then rewind the flat block into a coil, and cold-rolled to reduce the flatness obtained by the coil by 70% to 96% The obtained cold-rolled alloy sheet is annealed to 420 ° C to 500 ° C at a temperature of 5 ° C / second or more at a temperature rise rate of 5 ° C / second or more. The aluminum alloy plate of the present invention defines a chemical composition range and a microstructure range, and uniformly and precisely disperses intermetallic compounds. Therefore, by improving the crystal grain size 200540280 degrees to improve the formability at high temperature and high speed without any high purity metal, And can reduce the cavity after forming. -In addition, the manufacturing method of the present invention can obtain high cooling rate in Jingshi by restricting cold rolling and thinning, and limiting annealing conditions after cold drying. 5 Therefore, the uniform dispersion of intermetallic compounds can be precisely dispersed and improved. Fineness of crystal grains. By using the Shao alloy plate of the present invention, advanced shaped products can be obtained. • The forming time is shortened and productivity is improved. [Square package] 10 Detailed description of the preferred embodiment It will explain the reason for limiting the chemical composition of the alloy of the present invention. Unless otherwise stated, "%", which indicates the chemical composition in this specification, means "Wt%". [Mg · 2.0-8.0%] Element of good strength. In order to exhibit this effect, the magnesium content must be set to 2.0% or more. However, if the town content exceeds 8.0%, the thickness of the thin flat pieces is low. The lock content is limited to 2 • ⑽ to 8 • ⑽. If emphasis is placed on prayerfulness, then the preferred town content is further limited to 6.0% or less. [Si. 0.06-0.2%] 2〇A1 p ^. Dagger 1 mainly, fine particles of Mgji, and other intermetallic compounds ^ Moreover, Shi Xi was used as the site of recrystallization nucleus production during annealing after cold-drying Moon dagger. In this way, the greater the number of particles of these intermetallic compounds, the greater the number of nuclei produced. As a result, the number of fine recrystallized grains formed was 4 large. In addition, the recrystallization of the metallurgical compound S3, 200540280, was crystallized. The grain boundaries of the grains are restrained from growing due to the merging of the crystal grains, and the fine recrystallized grains are stably maintained. In order to exert these effects, it is necessary to set the silicon content to 0 06% or more. However, if the silicon content exceeds 0.2%, the tendency of the precipitated intermetallic compound to become coarser 5 becomes stronger, thereby promoting the formation of cavities during high-temperature deformation. As such, the silicon content is limited to 0.06% to 0.2%. A preferred range is from 7% to 0.15%. In general, silicon is regarded as an impurity element and is intended to be removed in the same manner as iron described later. However, in the present invention, there is an appropriate amount of stone syrup to increase the fineness of the recrystallized grains as described above. This eliminates the need for high-purity metals and does not accompany the increase of 10 points. 15
20 鐵於洗鑄時係呈基於腳⑽或其它金屬間化合物之 細小晶粒而沉殿，且於冷軋後於退火時係作為再結晶之孕 核產生位置。如此，此等金屬間化合物之粒子數目愈多， 則產生之再結晶孕核數目愈多，結果形紅細小再結晶晶 淨數目,¾大。此外’金屬間化合物之細小粒子固定所產生 之再結晶日日日粒之晶粒邊界’由於晶體晶粒的合併而抑制成 長，可穩定維持細小再結晶晶粒。為了發揮此等效果’需 要讓鐵含量為〇.1%或以上。但若鐵含量超過〇5%，則沉^ 之金屬間化合物變粗大之趨勢變強，因而促成高溫變形時又 的空腔形成。如此’鐵含量被限於〇.1%至 為 〇撕 〇.3%。 _ 同前述矽之相同方 里鐵，來提兩如前 通常’鐵被視為雜質元素而欲以如 式去除，但於本發明，相反地存在有適 9 200540280 述再結晶晶粒之細度。如此無需高純度金屬，也未伴隨成 分的增高。 [Μη ： 0.1-0.5%] 猛為增加再結晶晶粒之細度之元素。為了發揮此種效 5果，需要讓錳含量為0.1%或以上。但若錳含量超過0.5%， 則形成粗大之基於A1_(Fe.Mn)_Si之金屬間化合物，促成高 溫變形時出現空腔。如此，錳含量係限於〇1%至〇5%。特 另J菖加G預防空腔的出現時，較佳猛含量之上限進一步限 於0.3% 〇 10 [選擇性成分Cu : 〇·1-〇·5%] 本發明中，鋼添加量可於〇1_〇 5%之範圍俾改良鋁合金 板之強度。為了充分維持沉殿之硬化效果，須將銅添加量 周正為0.1%或以上。但若鋼添加量超過0.5%，則洗禱性降 -田強调/疋鑄性日守，較佳銅添加量之上限進一步限於0 3 % 15 或以下。 、θ /為了輔助提高再結晶後晶粒之細度，可摻 ^圍之至 聽及絡。錯及鉻為增加再結晶晶 粒細度之元素。為了表 20 量為〇.1%或以上，私力^果，需要讓鍅及鉻之添加 粗大之金屬間化合物^Γ過㈣，則於祕時形成 當強調避免出現空腔時，=㈣促成空腔的形成。特別 或以下。 土添加量上限進一步限於0.2% [其它元素] 10 200540280 本舍月中為了提高洗鑄結構之細度，可添加 0.001-0.15%耗圍之鈦。為了表現此種效果，需要讓鈦之添 加量為0.001%或以上。但若鈦添加量超過〇15%，則產生粗 大化合物諸如TiAl3，於高溫之成形性低劣，促成空腔之形 成。較佳鈦含量範圍為〇〇〇6_〇 1〇%。 其次將說明限制本發明之合金板之顯微結構之理由。 [具有當量圓直徑1微米至5微米之金屬間化合物之密 度為5000/平方毫米或以上] 本舍明利用細小金屬間化合物粒子作為⑴再結晶後晶 10粒孕核之產生位置；及(2)固定再結晶後晶粒之晶粒邊界， 於冷乳後藉退火產生較為精細之再結晶晶粒之手段。藉此 方式所得之細小晶粒結構可於高溫高速下，於變形時獲得 高度伸長率。藉此於高溫及高速下之成形性提升。 為了獲得前述效果，具有當量圓直徑1微米至5微米之 15金屬間化合物須以50GG/平方毫米或以上之密度存在。至於 金屬間化合物’如前文說明，諸如基於A1_(FeMn)_si之化 合物、MgA及Al6Mn等金屬間化合物於洗禱期間沉殿。為 了由此等金屬間化合物來表現如上⑴及⑺之效果，當量圓 直徑係為1微米至5微米。若當量圓直徑係小於】微米，則粒 2〇子過小而無法表現前述⑴及(2)之效果。相反地，若當量圓 直徑超過5齡，躲高溫高速下，於變形時容^產生空腔 ，故成形後之強度及伸長率下降。 具有尺寸於前述範圍之金屬間化合物須以5000/平方 毫米或以上之密度存在。 200540280 若雀度係低於5000/平方毫米，則退火時之再結晶後之 晶粒直徑超過20微米，且於高溫變形時之伸長率下降。 [平均晶體晶粒直徑為2〇微米或以下] 於本發明之合金板，將平均晶體晶粒直徑調整為2〇微 米或以下。若平均晶體晶粒直徑超過2〇微米，則高溫變形 時之伸長率下降。 其次將說明限制本發明之製造方法之條件之理由。 [藉雙帶洗鑄而具有厚度5毫米至15毫米之扁塊係呈盤 捲形式捲取] 10 15 20 雙帶澆_法為連續洗鑄 … w 对俗Μ田/從平寻f _端，於 垂直方向將熔體注人由—對彼此面對面之水冷式旋轉帶所 製成之模具内’由帶表面冷卻來固化㈣形成扁塊，將成 形後之扁塊由模具的另—端抽出，將扁塊捲取成為盤捲形 式。 本發明中，藉此種雙帶庚铸法所堯鑄之扁塊厚度輕 為5毫米至15以。當厚度係於此範_，即使於合全板厚 度中部仍可獲得高固化速度，因此容㈣成均勾之: 構。同理’使用本發明組成物，容易抑制粗大金^化： 物的產生’變成容易控制最終板狀產物之再結晶後晶歡 平均晶粒>大小為顺米或以下。由雙帶料觀點，也適合 使用前文說明之扁塊厚度範圍。 換言之，若扁塊厚度小於5毫米 镇鋁么全熔雜曰、Μ 1 、j母早位日寸間通過澆 口至W!過小，故雙帶堯鑄變困 度超過15毫米，則變成難以再捲取成為盤捲形式。‘子 12 200540280 [於澆鑄時之冷卻速率為20至150°C/秒] 於本發明之製造方法，具有厚度5毫米至15毫米之扁塊 係藉雙帶澆鑄而澆鑄。此時，為了造成具有對本發明合金 規定之當量圓直徑1微米至5微米，且具有密度5000/平方毫 5 米或以上之金屬間化合物之沉澱，澆鑄期間，於扁塊1/4厚 度位置之冷卻速率調整為20至150°C/秒。於本發明之銘合 金，金屬間化合物諸如基於Al-(Fe.Mn)-Si之化合物及Mg2Si $ 於澆鑄時沉澱。若沉澱速率係低於2〇°C/秒，則金屬間化合 物變粗大，超過5宅米之化合物增加。相反地，若冷卻速率 10超過150 C/秒，則金屬間化合物變精細，小於丨微米之化合 物增加。結果，任一種情況下具有當量圓直徑丨微米至5微 米之金屬間化合物之密度變成小於5〇〇〇/平方毫米，於最終 退火時(CAL)，再結晶後之孕核數目變少，故再結晶晶粒變 粗大。 [冷乳減涛7 0至9 6 %之冷車匕j • 繞金屬間化合物藉冷乳進行雜加J1，結果發生差 排的累積，此乃最終退火時形成細小再結晶結構所不可或 缺。若冷軋減薄係小於70%，差排的累積變不足，無法獲 得細小之再結晶結構。若冷乾減薄超過96%，則冷乳期= 20 發生邊緣斷裂，讓冷軋變困難。 [以溫度升高速率5°C/秒或以上加熱退火至WC至500 t] 本發明中，前述退火係於冷軋後進行作為最终退火。 通常係藉連續退火而進行，但無需將退火特別限制於此。 13 200540280 最終退火之退火溫度為420°C至500°C之範圍。若溫度 低於420°C，則再結晶所需能量不足，故再結晶變不足，因 而無法獲得細小再結晶結構。但若溫度超過500°C，則再 結晶後之晶粒直徑超過20微米，無法獲得細小之再結晶結 5 構。 加熱至退火溫度之加熱速率調整為5°C/秒或以上。若 於低於5°C/秒之速率緩慢升高溫度，則再結晶晶粒變粗大 ，因而無法獲得細小之再結晶結構。 最後，本發明之鋁合金板之成形較佳係於400-500°C之 10 溫度進行。若成形溫度係低於400°C，則無法獲得足夠伸長 率。若成形溫度係超過550°C，則出現晶體晶粒變粗大。此 外，於含高錳含量於本發明範圍之合金出現燃燒，伸長率 降低。成形時之應變速率較佳為0.1/秒或以上。若應變速率 係低於0.1/秒，則成形期間出現晶體晶粒變粗大，因而誘生 15 伸長率的下降。 實施例 具有表1所示組成之鋁合金熔體係藉雙帶澆鑄法澆鑄 來形成厚7毫米至9毫米之扁塊。各個扁塊被冷軋至1毫米厚 度及於450°C退火，然後切出JIS H7501規定之試驗件，於 20 抗拉試驗之後接受伸長率之測定。此外，斷裂之試樣之截 面經過拋光，然後藉影像分析器來測定空腔面積比（空腔 比）。該製法及特徵顯示於表2。 14 200540280 表1 :合金組成（wt%) 合金 Mg Μη Fe Si Cu Zr A 3.1 0.3 0.12 0.07 - - B 5.2 0.3 0.15 0.10 - - C 7.1 0.4 0.10 0.09 - - D 3.2 0.2 0.12 0.07 0.3 - E 3.2 0.2 0.12 0.07 - 0.2 表2 :方法及特徵 試 樣 號 碼 合 金 扁塊 厚度 (毫来) 冷卻 速率 cam 板厚度 (毫米） 金屬 間化 合物 退火 (°C) 最終 板厚 度 (毫米) 冷 軋 減 薄 (%) 晶體晶 粒大小 (微米） 金屬間化合 物組成密度 (/平方毫米) 拉張 溫度 (°C) 抗拉 速度 (/秒） 伸 長 率 (%) 空腔 比 (%) 備註 1 A 8 75 - - 1 88 10 6233 500 0.5 231 0.23 Inv. 2 B 9 73 - - 1 89 7 7501 500 0.5 252 0.27 Inv. 3 C 7 78 - - 1 86 8 6145 500 0.5 270 0.19 Inv. 4 D 8 75 - - 1 88 9 6345 500 0.5 243 0.24 Inv. 5 E 8 75 - - 1 88 7 6433 500 0.5 255 0.25 Inv. 6 C 7 78 - - 1 86 8 6145 450 0.5 250 0.17 Inv. 7 C 7 78 - - 1 86 8 6145 500 0.25 201 0.15 Inv. 8 A 5 300 - - 1 88 68 2574 500 0.5 80 0.12 Comp. TRC 9 A 400 5 熱軋板 厚度： 7毫米 - 1 86 25 2890 500 0.5 160 1.5 Comp. DC 10 A 8 75 2 350 1 50 23 6844 500 0.5 101 0.54 Comp. 11 A 8 75 - - 1 88 10 6233 350 0.5 89 0.24 Comp. 12 A 8 75 - - 1 88 10 6233 500 0.01 138 1.8 Comp.20 Iron was sunk in the form of fine grains based on the fetters or other intermetallic compounds during washing and casting, and it was used as the nucleation site for recrystallization during annealing after cold rolling. In this way, the greater the number of particles of these intermetallic compounds, the greater the number of recrystallized nuclei produced, with the result that the net number of fine red recrystallized crystals is larger. In addition, "grain boundaries of recrystallized grains produced by the fixation of fine particles of intermetallic compounds" are suppressed due to the merging of crystal grains, and the fine recrystallized grains can be stably maintained. In order to exert these effects', the iron content needs to be 0.1% or more. However, if the iron content exceeds 05%, the tendency of the intermetallic compounds to become thicker becomes stronger, thereby promoting the formation of cavities during high-temperature deformation. In this way, the iron content is limited to 0.1% to 0.3%. _ The same square iron as the aforementioned silicon, to mention two. As usual, iron is considered as an impurity element and is intended to be removed in accordance with the formula, but in the present invention, on the contrary, there is a fineness of recrystallized grains as described in 9 200540280 . This eliminates the need for high-purity metals and does not accompany the increase in composition. [Μη: 0.1-0.5%] An element that sharply increases the fineness of the recrystallized grains. In order to exert this effect, the manganese content needs to be 0.1% or more. However, if the manganese content exceeds 0.5%, a coarse intermetallic compound based on A1_ (Fe.Mn) _Si is formed, which promotes the occurrence of cavities during high-temperature deformation. As such, the manganese content is limited to 0.001% to 5%. In addition, the upper limit of the preferable content when J 菖 Plus G is used to prevent the appearance of cavities is further limited to 0.3% 〇10 [Selective component Cu: 〇 · 1-〇 · 5%] In the present invention, the amount of steel can be added to 〇 1 ~ 05% range 俾 Improve the strength of aluminum alloy plate. In order to fully maintain the hardening effect of Shen Dian, the amount of copper added must be 0.1% or more. However, if the amount of steel added exceeds 0.5%, the prayer will be reduced. Tian Tian emphasized / casting day guard, the upper limit of the preferred copper addition is further limited to 0 3% 15 or less. , Θ / In order to help improve the fineness of the crystal grains after recrystallization, it can be blended to the ear. Chromium is an element that increases the fineness of recrystallized grains. In order to make the amount in Table 20 0.1% or more, it is necessary to let the addition of 鍅 and chromium add a thick intermetallic compound ^ Γ, and it is formed in secret. When it is emphasized to avoid cavities, ㈣ promotes Formation of cavities. Special or below. The upper limit of the amount of soil added is further limited to 0.2% [Other elements] 10 200540280 In order to improve the fineness of the wash-cast structure during the month, 0.001-0.15% of titanium consumed can be added. In order to exhibit this effect, it is necessary to make the amount of titanium added to be 0.001% or more. However, if the addition amount of titanium exceeds 0.15%, coarse compounds such as TiAl3 are produced, and the formability at high temperatures is poor, which promotes the formation of cavities. The preferred titanium content is in the range of 0.006 to 10%. The reason for limiting the microstructure of the alloy plate of the present invention will be explained next. [Density of intermetallic compounds with equivalent circle diameters of 1 micrometer to 5 micrometers is 5000 / mm 2 or more] Ben Shoming uses fine intermetallic compound particles as the location of the 10 pregnant nuclei of crystals after recrystallization of plutonium; and ) The grain boundaries of the recrystallized grains are fixed. After cold milking, annealing is used to generate finer recrystallized grains. The fine grain structure obtained in this way can obtain a high elongation during deformation at high temperature and speed. This improves the formability at high temperatures and speeds. In order to obtain the aforementioned effect, 15 intermetallic compounds having an equivalent circle diameter of 1 micrometer to 5 micrometers must be present at a density of 50 GG / mm 2 or more. As for the intermetallic compound ', as described above, intermetallic compounds such as compounds based on A1_ (FeMn) _si, MgA, and Al6Mn are sunk during the baptism. In order for such intermetallic compounds to exhibit the effects of ⑴ and ⑺, the equivalent circle diameter is 1 to 5 m. If the equivalent circle diameter is less than [micro] m, the particles 20 are too small to exhibit the effects of the above-mentioned ⑴ and (2). On the contrary, if the diameter of the equivalent circle exceeds 5 years old, and the high temperature and high speed are used, the cavity will be generated during deformation, so the strength and elongation after forming will decrease. Intermetallic compounds having a size in the foregoing range must be present at a density of 5000 / mm2 or more. 200540280 If the bird's degree is less than 5000 / mm2, the grain diameter after recrystallization during annealing exceeds 20 microns, and the elongation decreases when deformed at high temperature. [Average crystal grain diameter is 20 micrometers or less] In the alloy plate of the present invention, the average crystal grain diameter is adjusted to 20 micrometers or less. If the average crystal grain diameter exceeds 20 micrometers, the elongation at the time of high-temperature deformation decreases. Next, the reasons for limiting the conditions of the manufacturing method of the present invention will be explained. [By using double-belt washing and casting, flat pieces with a thickness of 5 mm to 15 mm are wound in the form of coils] 10 15 20 Double-belt pouring method is continuous washing and casting ... In the vertical direction, the melt is injected into a mold made of water-cooled rotating belts facing each other. The surface of the belt is cooled to solidify and form a flat block, and the formed flat block is drawn from the other end of the mold. , Take the flat block into coil form. In the present invention, the thickness of the flat block cast by this double-belt casting method is 5 mm to 15 mm. When the thickness is in this range, high curing speed can still be obtained even in the middle of the thickness of the whole board, so Rong Hongcheng has a uniform structure. In the same way, using the composition of the present invention, it is easy to suppress coarse metallization: the generation of the material becomes easy to control the final plate-like product after recrystallization. The average crystal grain size > From the perspective of dual tape, it is also suitable to use the flat block thickness range described above. In other words, if the thickness of the flat block is less than 5 mm, the full fusion of the aluminum alloy, M1, j through the gate to W! Is too small, so the double-belt casting becomes more difficult than 15 mm, and it becomes difficult. Rewind it into coil form. ‘Sub 12 200540280 [Cooling rate during casting is 20 to 150 ° C / sec] In the manufacturing method of the present invention, flat pieces having a thickness of 5 mm to 15 mm are cast by double-belt casting. At this time, in order to cause precipitation of intermetallic compounds having an equivalent circle diameter of 1 micrometer to 5 micrometers specified for the alloy of the present invention and a density of 5000 / square millimeter 5 meters or more, during casting, the The cooling rate is adjusted to 20 to 150 ° C / second. In the present invention, intermetallic compounds such as Al- (Fe.Mn) -Si based compounds and Mg2Si $ are precipitated during casting. If the precipitation rate is lower than 20 ° C / sec, the intermetallic compound becomes coarse, and the compound exceeding 5 m2 increases. Conversely, if the cooling rate 10 exceeds 150 C / sec, the intermetallic compound becomes finer, and the compound smaller than 丨 micron increases. As a result, in any case, the density of the intermetallic compound having an equivalent circle diameter of from 1 μm to 5 μm becomes less than 5000 / square millimeter. At the final annealing (CAL), the number of pregnant nuclei after recrystallization becomes smaller, so The recrystallized grains become coarse. [Cold milk reduction of 70 to 96% of the cold car dagger] • The addition of cold milk around the intermetallic compound J1 results in the accumulation of differential rows, which is indispensable for the formation of a fine recrystallized structure during final annealing. . If the cold rolling reduction is less than 70%, the accumulation of differential rows becomes insufficient, and a fine recrystallized structure cannot be obtained. If the cold-drying reduction exceeds 96%, the cold milking period = 20 causes edge breakage, making cold rolling difficult. [Thermal annealing at a temperature rising rate of 5 ° C / sec or more to WC to 500 t] In the present invention, the aforementioned annealing is performed after cold rolling as the final annealing. Usually, it is performed by continuous annealing, but it is not necessary to specifically limit annealing to this. 13 200540280 The annealing temperature for the final annealing is in the range of 420 ° C to 500 ° C. If the temperature is lower than 420 ° C, the energy required for recrystallization is insufficient, so recrystallization becomes insufficient, and a fine recrystallized structure cannot be obtained. However, if the temperature exceeds 500 ° C, the grain diameter after recrystallization exceeds 20 microns, and a fine recrystallized structure cannot be obtained. The heating rate for heating to the annealing temperature is adjusted to 5 ° C / second or more. If the temperature is slowly raised at a rate of less than 5 ° C / sec, the recrystallized grains become coarse, and thus a fine recrystallized structure cannot be obtained. Finally, the forming of the aluminum alloy plate of the present invention is preferably performed at a temperature of 400-500 ° C. If the forming temperature is lower than 400 ° C, a sufficient elongation cannot be obtained. When the forming temperature exceeds 550 ° C, crystal grains become coarse. In addition, the alloy containing a high manganese content within the range of the present invention burns and the elongation decreases. The strain rate during forming is preferably 0.1 / second or more. If the strain rate is less than 0.1 / sec, coarsening of crystal grains occurs during forming, and thus a decrease in elongation is induced. Example An aluminum alloy melting system having the composition shown in Table 1 was cast by a two-belt casting method to form a flat block having a thickness of 7 mm to 9 mm. Each flat block was cold-rolled to a thickness of 1 mm and annealed at 450 ° C, then a test piece specified in JIS H7501 was cut out, and the elongation was measured after a tensile test. In addition, the section of the fractured sample was polished, and the cavity area ratio (cavity ratio) was measured by an image analyzer. The manufacturing method and characteristics are shown in Table 2. 14 200540280 Table 1: Alloy composition (wt%) Alloy Mg Mn Fe Si Cu Zr A 3.1 0.3 0.12 0.07--B 5.2 0.3 0.15 0.10--C 7.1 0.4 0.10 0.09--D 3.2 0.2 0.12 0.07 0.3-E 3.2 0.2 0.12 0.07-0.2 Table 2: Method and characteristics Sample number Thickness of alloy block (millions) Cooling rate cam Plate thickness (mm) Intermetallic compound annealing (° C) Final plate thickness (mm) Cold rolling reduction (%) Crystal Grain size (micron) Intermetallic compound density (/ mm2) Tensile temperature (° C) Tensile speed (/ s) Elongation (%) Cavity ratio (%) Remarks 1 A 8 75--1 88 10 6233 500 0.5 231 0.23 Inv. 2 B 9 73--1 89 7 7501 500 0.5 252 0.27 Inv. 3 C 7 78--1 86 8 6145 500 0.5 270 0.19 Inv. 4 D 8 75--1 88 9 6345 500 0.5 243 0.24 Inv. 5 E 8 75--1 88 7 6433 500 0.5 255 0.25 Inv. 6 C 7 78--1 86 8 6145 450 0.5 250 0.17 Inv. 7 C 7 78--1 86 8 6145 500 0.25 201 0.15 Inv. 8 A 5 300--1 88 68 2574 500 0.5 80 0.12 Comp. TRC 9 A 400 5 Hot rolled sheet thickness: 7 mm-1 86 25 2890 500 0.5 16 0 1.5 Comp. DC 10 A 8 75 2 350 1 50 23 6844 500 0.5 101 0.54 Comp. 11 A 8 75--1 88 10 6233 350 0.5 89 0.24 Comp. 12 A 8 75--1 88 10 6233 500 0.01 138 1.8 Comp.
5 註）再結晶晶粒係錯十字切割法測定。 冷卻速率係由於澆鑄扁塊之1/4厚度處之DAS測量結果計算。 經由冷軋雙帶澆鑄機所得之薄扁塊獲得之板（本發明 產品，試樣號碼1至7)由表1之合金組成顯然易知，與全部 10 試樣之鐵含量為0.1%或以上，以及矽含量為0.06%或以上無 關，本發明產物具有當量圓直徑1微米至5微米之金屬間化 合物之密度為5(K)0/平方毫米或以上，以及具有晶體晶粒大 15 200540280 小為20微米或以下。因此理由故，於拉張溫度5〇〇t之伸長 率良好，為200%或以上；高溫拉張後之空腔比為良好，於 0.15-0.27%或小於1%之範圍。5 Note) Recrystallized grains are determined by cross cutting method. The cooling rate is calculated from the DAS measurement results at 1/4 of the thickness of the cast flat block. The plate obtained from the thin flat block obtained by the cold-rolled double-strip casting machine (product of the present invention, sample numbers 1 to 7) is obviously easy to know from the alloy composition of Table 1, and the iron content of all 10 samples is 0.1% or more Regardless of the silicon content being 0.06% or more, the product of the present invention has an equivalent circle diameter of 1 micrometer to 5 micrometers and an intermetallic compound with a density of 5 (K) 0 / mm 2 or more, and has a crystal grain size of 15 200540280 small. It is 20 microns or less. For this reason, the elongation at a tensile temperature of 500t is good, which is 200% or more; the cavity ratio after high-temperature stretching is good, in the range of 0.15-0.27% or less than 1%.
經由冷軋藉雙輥澆鑄機洗鑄所得之薄扁塊獲得之合金 5 板（比較例，試樣號碼8)含有大量極為細小之具有當量圓直 徑小於1微米之金屬間化合物，原因在於澆鑄時之冷卻速率 相對較高，為30(TC/秒，故最終合金板之具有當量圓直秤 為1微米至5微米之金屬間化合物之密度係小於平方 毫米，或其晶粒粗大超過晶體晶粒大小20微米或以上。因 10 此理由故，高溫拉張後之空腔比相當低而良好，空腔比為 0.12%，但於500°C拉張溫度之伸長率不佳，為8〇%。 藉直流澆鑄機澆鑄所得尋常扁塊，經由浸泡，然後熱 軋扁塊至7毫米厚度，然後冷軋（比較例，試樣號碼9)獲得之 板於澆鑄時之冷卻速率相對較低，為5°C/秒，故產生具有 15 當量圓直徑超過5微米之金屬間化合物，因此最終所得合公 板之具有當量圓直徑為1微米至5微米之金屬間化合物之资 度變成低於5000/平方毫米，晶體晶粒變成略為粗輪，超過 20微米。因此理由故，於高溫拉張測試後之空腔比不佳， 空腔比高達1.5%，而於拉張溫度500°C之伸長率不佳，伸香 20 率為 160%。 經由將雙帶澆鑄機澆鑄之薄扁塊冷軋至板厚度為 米，然後於350°C中間退火扁塊，然後冷軋至1毫米獲得之 合金板（比較例，試樣號碼10)具有最終所得板之當量圓直押 1微米至5微米之金屬間化合物密度為5000/平方毫米气以 16 200540280 上，但最終退火前之冷軋減薄低，冷軋減薄低於70%，因 此晶體晶粒變成略為粗大，超過晶體晶粒大小20微米。於 拉張溫度500。0之伸長率不佳，伸長率低於200%。 經由冷軋由雙帶洗鑄機澆鑄所得之薄扁塊獲得之合金 5 板（比較例，試樣號碼n)具有最終形成之板中具有當量圓直 徑1微米至5微米之金屬間化合物密度為5000/平方毫米或 以上，以及晶體晶粒大小為20微米或以下。但拉張測試之 拉張溫度相當低，為350°C，故伸長率不佳，伸長率係低於 200〇C 〇 10 經由冷軋由雙帶澆鑄機澆鑄所得之薄扁塊獲得之合金 板（比較例，試樣號碼12)具有最終形成之板中具有當量圓直 徑1微米至5微米之金屬間化合物密度為5000/平方毫米或 以上，以及晶體晶粒大小為20微米或以下。但拉張測試之 拉張速度相當慢，為0.01/秒，故於高溫拉張後之空腔比也 15 不佳，為1.8% ;於500°C拉張溫度之伸長率為不佳，低於 200% 〇 產業應用性 根據本發明’可提供一種有較少量空腔且於高溫南速 下具有優異成形性之鋁合金板，及其製造方法。 20 【圖式簡單說明】 (無） 【主要元件符號說明】 (無） 17The alloy 5 plate (comparative example, sample number 8) obtained by cold-rolling the thin flat block obtained by washing and casting with a two-roll caster contains a large amount of extremely small intermetallic compounds having an equivalent circle diameter of less than 1 micron, because The cooling rate is relatively high, which is 30 ° C / sec. Therefore, the density of the intermetallic compound with an equivalent circular straight scale of 1 to 5 microns in the final alloy plate is less than square millimeters, or its grain size is larger than the crystal grain size. The size is 20 microns or more. For this reason, the cavity ratio after high temperature stretching is quite low and good. The cavity ratio is 0.12%, but the elongation at 500 ° C stretching temperature is not good, which is 80%. The ordinary flat block obtained by DC casting machine was immersed, then hot-rolled the flat block to a thickness of 7 mm, and then cold-rolled (comparative example, sample number 9). The cooling rate of the plate during casting was relatively low. 5 ° C / s, so intermetallic compounds with 15 equivalent circle diameters exceeding 5 micrometers are produced, so the qualification of intermetallic compounds with equivalent circle diameters of 1 micrometer to 5 micrometers obtained in the final hegong board becomes less than 5000 / Mm2, The bulk grains become slightly coarser, exceeding 20 microns. Therefore, the cavity ratio after the high temperature tensile test is not good, the cavity ratio is as high as 1.5%, and the elongation at the tensile temperature of 500 ° C is not good. The rate of Nobori 20 is 160%. The alloy sheet obtained by cold rolling a thin flat block cast by a double-belt casting machine to a thickness of meters, then annealing the flat block at 350 ° C, and then cold rolling to 1 mm (Comparative Example) (Sample No. 10) The density of the intermetallic compound with an equivalent circle of 1 micrometer to 5 micrometers in the final plate obtained is 5000 / square millimeter gas on 16 200540280, but the cold rolling reduction before the final annealing is low and the cold rolling reduction is The thinness is less than 70%, so the crystal grains become slightly coarse, exceeding the crystal grain size by 20 microns. The elongation at a tensile temperature of 500.0 is not good, and the elongation is less than 200%. Washing and casting from double bands through cold rolling An alloy 5 plate (comparative example, sample number n) obtained from a thin flat block obtained by machine casting has a density of 5000 / mm 2 or more of an intermetallic compound having an equivalent circle diameter of 1 to 5 μm in the finally formed plate, and The crystal grain size is 20 microns or less. But The tensile temperature of the tensile test is quite low, which is 350 ° C, so the elongation is not good. The elongation is less than 200 ° C. 〇10 The alloy plate obtained by cold-rolling a thin flat block cast by a two-belt casting machine (comparison For example, sample number 12) The density of the intermetallic compound having an equivalent circle diameter of 1 micrometer to 5 micrometers in the finally formed plate is 5000 / mm 2 or more, and the crystal grain size is 20 micrometers or less. But tensile test The stretching speed is quite slow, 0.01 / second, so the cavity ratio after high temperature stretching is also poor, which is 1.8%; the elongation at 500 ° C stretching temperature is not good, less than 200%. Industrial Applicability According to the present invention, it is possible to provide an aluminum alloy plate having a small number of cavities and excellent formability at a high temperature and a south speed, and a method for manufacturing the same. 20 [Schematic description] (None) [Description of main component symbols] (None) 17