1299755 (1) 玖、發明說明 【發明所屬技術之領域】 本發明係針對在沖壓成形後或成形前連續電阻點熔 ，將製品組裝的家電製品或汽車的外裝殼板乃至其他構 材，關於具有優異的沖壓成形性及連續電阻點熔接性的 合金板及其製造方法。 【先前技術】 家電產品或汽車的外裝殼板乃至其他的構造材係進 有在沖壓成形後將各構成構件電阻點熔接而組裝製品。1299755 (1) 玖 发明 发明 发明 发明 发明 发明 发明 发明 发明 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 】 An alloy sheet having excellent press formability and continuous resistance spot weldability and a method for producing the same. [Prior Art] Household appliances, automotive exterior panels, and other structural materials are assembled by welding the resistance points of the constituent members after press forming.
Al— Mg— Si系之JIS6000系合金板，係因爲沖壓 形後的加工面最後加工成比較美觀，所以雖然可使用在 種的外裝殼板及構造材，但是從製品形狀的多樣化要求 良好的沖壓成形性。 另外，從生產性提高的觀點，爲了減少電阻點熔接 業時的電極交換次數，因此要求有電阻點熔接的連續熔 次數之提高。 至於J I S 6 0 0 0系的板，例如在專利文獻}(日本特 昭62-20785 1號公報）係作爲成形加工性之良好的車體 板（body sheet)等的壓延板的製造方法，在同公報的 請專利範圍第4項是記載有：含有Si: 0.4〜2.5%、Mg 0.1〜1.2%，含有從Cu : 1 .5%以下、Zn : 2.5%以下、 :0.3%以下' Μη: 0.6%以下、Zr: 0.3 %以下之中所 擇1種或2種以上，將剩餘部份由A1及不可避免的不 接 造 鋁 行 成 各 有 作 接 開 薄 串 Cr 選 純 -5- (2) 1299755 物所組成的鋁合金熱熔液連續鑄造成板厚3〜1 5 m m的 板，其後施予了冷軋後，進行固溶處理（solution treatment )·淬火爲其特徵的鋁合金壓延板的製造方法。 另外，在專利文獻2(日本特開2001— 262264號公 報）係作爲彎曲性良好的汽車材板（car panel )等的素材 ，在同公報的申請專利範圍第1至3項是具有：在申請專 利範圍第1項，以mass%，來將Mg : 0.1〜2.0%、Si ·· 0.1〜2.0%、Fe : 0·1〜1 .5%及剩餘部份A1作成爲本質的 成分，Fe、Si系化合物的最大粒子徑爲5 // m以下，並且 平均結晶粒徑爲3 0 // m以下，對韌性及彎曲性優異的A1 一 Mg - Si系 A1合金板；在申請專利範圍第2項，以 mass%，將 Mg: 0.1 〜2.0%、Si: 0.1 〜2.0%、Fe: 0·1 〜 1.5%、Cu : 2.0%以下及剩餘部份A1作成爲本質的成分 ，Fe、Si、Cu系化合物的最大粒子徑爲5 // m以下，並且 平均粒徑爲3 0 // m以下，對韌性及彎曲性優異的A1 一 Mg 一 Si系人1合金板；及在申請專利範圍第3項，更記載於 含有從由Mn: 1.0%以下、Cr: 0.3%以下、Zr: 0.3%以 下、V : 0.3%以下、Ti : 0·03%以下組成的群組所選擇的 1種以上之成分的申請專利範圍第丨項或第2項的A1 -Mg - Si系A1合金板的記載。 【專利文獻1】日本特開昭62-2078 5 1號公報（申請 專利範圍第4項’曰文說明書第4頁左上欄下第5行〜同 頁左上欄第1 1行） 【專利文獻2】日本特開2〇〇1·262264號公報（申請 (3) 1299755 專利範圍第1、2、3項，段落編號〔0028〕） 【發明內容】 〔發明所欲解決之課題〕 上述專利文獻1 (日本特開昭62-207 85 1號公報）所 揭示的技術是採用雙輥軋鑄造法（twin roll type casting method)，因爲以100°C/sec以上的冷卻速度使之凝固 ，所以鑄造時晶出的金屬間化合物的尺寸小，其結果由於 不能得到對再結晶時的結晶粒尺寸帶來影響之較大化合物 之充分的量，因此固溶處理後的結晶粒尺寸大而沖壓性差 ，另外電阻點熔接的連續次數少。 上述專利文獻2 (日本特開200 1 -262264號公報）所 揭示的技術是採用連續鑄造法，雖然以10°C / sec以上的 冷卻速度使之凝固，但是在實施例係採用以冷卻速度之最 大3 (TC / sec。因爲冷卻速度遲緩，所以鑄造時晶出的金 屬間化合物的尺寸大，其結果由於不能得到對再結晶時的 結晶粒尺寸帶來影響之較大化合物之充分的量，因此固溶 處理後的結晶粒尺寸大而沖壓性差，另外電阻點熔接的連 續打點次數少。 本發明的目的是提供具有優異的沖壓成形性及連續電 阻點熔接性的鋁合金板及其製造方法。 〔用以解決課題之手段〕 本發明者群爲了達成上述目的，在適切的組成範圍之 (4) 1299755 中將凝固時的熱熔液冷卻速度作爲最適的範圍之情況， 在晶出的金屬間化合物的尺寸以及個數之中謀求最適切 ’所獲得之固溶化後的鋁合金板是具有優異的沖壓成形 及連續電阻點熔接性的發現而開發完成本發明。 亦即本發明的第一發明是以質量％，由含有Mg ··( 〜1·0%、Si: 0.3 〜1.2%、Fe: 0.10 〜1.0% 及 Μη: 0· 〜0.5%，且Fe + Mug 0.2、剩餘部份Α1及不可避免的 純物所組成，再結晶粒徑的平均値爲2 5 // m以下，而 存在以相當圓徑爲1〜6//m的金屬間化合物5000個 mm2以上爲其特徵之具有優異的沖壓成形性及連續電阻 熔接性的鋁合金板。 以如此細微的再結晶粒尺寸，因爲最適切尺寸的化 物數多，所以具有優異的沖壓成形性及連續電阻點熔接 〇 在上述的組成更由於使Cii含有0.5〜1.0%，而強 更提高。 在上述的組成更由於使Zr含有0.1〜0.4%，而以 微的再結晶粒尺寸使強度更提高。 而且由於使之含有Ti爲0.05%以下或Ti爲0.05% 下及B爲0.01%以下，而更能確實地防止鑄造時的鑄 裂損。 本發明的第二發明係將上述組成的合金熱熔液注入 相對峙之被強制冷卻的旋轉帶式鑄模內’以熱熔液凝固 的冷卻速度40〜90°C/sec使之凝固而成厚度爲5〜 係 化 性 1.3 05 不 且 / 點 合 性 度 細 以 造 到 時 10 (5) 1299755 mm的厚板，從注入熱熔液的相反側拉出該厚板，直接或 從捲筒成渦狀來壓延並固溶處理作爲其特徵之具有優異的 沖壓成形性及連續電阻點熔接性的鋁合金板。 由於使本發明的合金熱熔液以最適切的凝固時之冷卻 速度凝固，而能使最適切尺寸的化合物多數晶出，微細化 再結晶粒尺寸而能獲得具有優異的沖壓成形性及連續電阻 點熔接性的鋁合金板。 〔發明效果〕 依據本發明的話，提供具有優異的沖壓成形性及連續 電阻點熔接性的鋁合金板及其製造方法。 【實施方式】 說明本發明的鋁合金板的各構成要件的限定理由。在 本說明書中顯示成分含有量「％」係「質量％」的意思。 〔Mg: 0.3 〜1.0%〕 〔Si : 0.3 〜1 .2%〕The Al-Mg-Si-based JIS6000-based alloy sheet is processed because the finished surface after stamping is finally beautiful. Therefore, although the outer shell and the structural material can be used, the shape of the product is required to be diversified. Stamping formability. Further, from the viewpoint of improvement in productivity, in order to reduce the number of electrode exchanges during the resistance spot welding, it is required to increase the number of continuous fusions of the resistance spot welding. In the method of manufacturing a rolled sheet such as a body sheet having a good formability, for example, a method of manufacturing a rolled sheet such as a body sheet having a good workability is used in the case of a JIS 960-based sheet. In the fourth item of the patent application, it is described that Si: 0.4 to 2.5%, Mg 0.1 to 1.2%, and Cu: 1.5% or less, Zn: 2.5% or less, and 0.3% or less 'Μη: 0.6% or less, Zr: 0.3% or less, one or two or more selected ones, and the remaining part is made of A1 and unavoidable aluminum. 2) The aluminum alloy hot melt composed of 1299755 is continuously cast into a plate having a thickness of 3 to 15 mm, and then subjected to cold rolling, and then subjected to solution treatment and quenching. A method of manufacturing a rolled sheet. In the patent document 2 (JP-A-2001-262264), it is a material of a car panel or the like which is excellent in flexibility, and the first to third items of the patent application of the same publication are: In the first item of the patent range, in mass%, Mg: 0.1 to 2.0%, Si · 0.1 to 2.0%, Fe: 0·1 to 1.5%, and the remaining part A1 are essential components, Fe, A1-Mg-Si-based A1 alloy sheet having a maximum particle diameter of 5 // m or less and an average crystal grain size of 3 0 // m or less, which is excellent in toughness and flexibility; In terms of mass%, Mg: 0.1 to 2.0%, Si: 0.1 to 2.0%, Fe: 0·1 to 1.5%, Cu: 2.0% or less, and the remaining portion A1 as essential components, Fe, Si, The A1-Mg-Si-based human 1 alloy plate having a maximum particle diameter of 5 // m or less and an average particle diameter of 3 0 // m or less, which is excellent in toughness and flexibility, and a patent application scope The three items are further described as being selected from the group consisting of Mn: 1.0% or less, Cr: 0.3% or less, Zr: 0.3% or less, V: 0.3% or less, and Ti: 0·03% or less. Patent application range of one or more kinds of components Shu item or the second item A1 -Mg - A1 describes Si based alloy sheet. [Patent Document 1] Japanese Patent Laid-Open No. 62-2078 5 No. 1 (Application No. 4 of the Patent Application No. 4 of the left-hand column of the fourth page of the manual, the first line of the upper left column of the same page) Japanese Laid-Open Patent Publication No. Hei. No. 2,262,264 (Application No. (3) 1299755, Patent No. 1, 2, and 3, Paragraph No. [0028]) [Problems to be Solved by the Invention] Patent Document 1 The technique disclosed in Japanese Laid-Open Patent Publication No. SHO-62-207 85 No. 1 is a twin roll type casting method. Since it is solidified at a cooling rate of 100 ° C/sec or more, it is cast. The size of the intermetallic compound crystallized is small, and as a result, a sufficient amount of a large compound which affects the crystal grain size at the time of recrystallization cannot be obtained, so that the crystal grain size after the solution treatment is large and the punchability is poor, and The number of consecutive times of resistance point welding is small. The technique disclosed in the above-mentioned Patent Document 2 (JP-A-200-262264) uses a continuous casting method, and although it is solidified at a cooling rate of 10 ° C /sec or more, in the embodiment, a cooling rate is employed. The maximum amount is 3 (TC / sec. Since the cooling rate is slow, the size of the intermetallic compound crystallized at the time of casting is large, and as a result, a sufficient amount of a large compound which affects the crystal grain size at the time of recrystallization cannot be obtained. Therefore, the crystal grain size after the solution treatment is large, the punchability is poor, and the number of consecutive dots of the resistance spot welding is small. The object of the present invention is to provide an aluminum alloy sheet having excellent press formability and continuous resistance spot weldability and a method for producing the same [Means for Solving the Problem] In order to achieve the above object, the inventors of the present invention have crystallized metal in the case where the hot melt cooling rate at the time of solidification is the optimum range in the appropriate composition range (4) 1299755. The alloyed aluminum alloy sheet obtained by optimizing the size and the number of inter-compounds is excellent in press forming and continuous The present invention has been developed by the discovery of the spot weldability. That is, the first invention of the present invention is based on mass%, containing Mg··(~1·0%, Si: 0.3 to 1.2%, Fe: 0.10 to 1.0%). And Μη: 0·~0.5%, and Fe + Mug 0.2, the remaining part Α1 and the unavoidable pure matter, the average 値 of the recrystallized grain size is 2 5 // m or less, and there is a considerable circular diameter An aluminum alloy sheet having excellent press formability and continuous electric resistance weldability, characterized by an intermetallic compound of 1 to 6/m, which is 5000 mm2 or more. With such a fine recrystallized grain size, the number of the most suitable size is There are many, so it has excellent press formability and continuous resistance spot fusion. In the above composition, the Cii contains 0.5 to 1.0%, and the strength is further improved. In the above composition, Zr is contained in the range of 0.1 to 0.4%. The micro-recrystallized grain size further increases the strength. Further, since Ti is contained in an amount of 0.05% or less, or Ti is 0.05%, and B is 0.01% or less, the casting crack during casting can be more reliably prevented. The second invention injects the alloy hot melt of the above composition into the opposite In the cooled rotating belt mold, the solidification temperature is 40 to 90 ° C / sec, and the solidification is carried out to a thickness of 5 to 1. The thickness is 5 to 1. The thickness is not good and the point is fine. 10 (5) 1299755 mm thick plate, which is pulled out from the opposite side of the hot melt, directly or from the roll to be rolled and calcined and solution treated as its characteristic, has excellent press formability and continuous The aluminum alloy sheet having the resistance point fusion property is obtained by solidifying the alloy hot melt of the present invention at the cooling rate at the time of optimum solidification, whereby a compound having an optimum size can be crystallized, and the recrystallized grain size can be obtained. An aluminum alloy sheet having excellent press formability and continuous resistance spot weldability. [Effect of the Invention] According to the present invention, an aluminum alloy sheet having excellent press formability and continuous resistance spot weldability and a method for producing the same are provided. [Embodiment] The reason for limiting the respective constituent elements of the aluminum alloy sheet of the present invention will be described. In the present specification, the meaning of the component content "%" is "% by mass". [Mg: 0.3 to 1.0%] [Si: 0.3 to 1.2%]
Mg及Si係爲了強度的提升和賦予沖壓成形性所添加 之物’在未滿下限値係效果少，一旦超過上限値的話沖壓 性就差而且不良。 〔Fe : 0.10 〜1.0%〕 〔Μη : 0.05 〜0.5%〕 * . . * 9 (6) 1299755 〔Fe+ Μη- 0.2%〕In the Mg and Si systems, the effect of increasing the strength and imparting press formability is less than the lower limit. When the upper limit is exceeded, the pressability is poor and poor. [Fe: 0.10 ～1.0%] [Μη: 0.05 ～0.5%] * . . * 9 (6) 1299755 [Fe+ Μη- 0.2%]
使Fe和Μη共存而且由於Fe+Mn^O.2%，而使特定 尺寸的化合物數多數晶出而增加在結晶核數，爲了細微化 再結晶粒的尺寸而添加。在兩元素均未滿下限値係效果少 ，一旦超過上限値的話粗大晶出物就產生，在冷軋時條紋 (streak )等的表面傷痕容易產生，另外沖壓性也差。當 Μη不和Fe共存時，較佳的尺寸並且多數的金屬間化合物 就不晶出。Fe及Μη的合計量較佳爲Fe+Mn20.3%。 〔C u : 0 · 5 〜1 · 0 %〕When Fe and Μη are coexisted and Fe+Mn^0.2%, the number of compounds of a specific size is mostly crystallized and increased in the number of crystal nuclei, and is added in order to refine the size of the recrystallized grains. When both elements are less than the lower limit, the effect is less. When the upper limit is exceeded, coarse crystal grains are generated, and surface flaws such as streaks are likely to occur during cold rolling, and the punchability is also poor. When Μη does not coexist with Fe, the preferred size and most of the intermetallic compounds do not crystallize. The total amount of Fe and Μη is preferably Fe + Mn 20.3%. [C u : 0 · 5 〜 1 · 0 %]
Cii是爲了使強度與沖壓成形性更提高而添加之物。 在未滿下限値係效果少，一旦超過上限値的話耐蝕性就降 低0 〔Zr : 0· 1 〜0.4%〕Cii is added to improve strength and press formability. In the case of less than the lower limit, the effect is less. If the upper limit is exceeded, the corrosion resistance is reduced to 0 [Zr : 0·1 to 0.4%]
Zr是促使Al3Zr的金屬間化合物的晶出，使特定尺寸 的化合物數更多數晶出而增加再結晶核數，爲了微細化再 結晶粒的尺寸而添加者，使之更微細再結晶而且提高沖壓 成形性。在未滿下限値係效果少，一旦超過上限値的話形 成粗大晶出物而壓延性就降低。 〔Ti: 0.05% 以下、或 Ti: 0.05% 以下及 B: 0.01% 以下 ) 在熱熔液凝固之際因急冷的原因而有產生鑄造裂損之 •10- (7) 1299755 虞，Ti或Ti及B是爲了防止裂損而添加，Ti: 0.05%以 下、或即使在B: 0.01%以下的範圍複合添加上述範圍之 Ti也可，特別是一旦使之複合含有Ti的話效果就相乘。 在使效果顯現化是Ti的下限値爲0.002%以上，B的下限 値爲0.0005%以上。 不可避免的不純物是從鋁基金屬、還原材、熔製治具 等混入之物，以Cr、Ni、Zn、Ga、V爲代表性的元素。 Cr是因爲防止A1 - Mg系合金的應力腐蝕裂損所添加，所 以雖然從還原材混入容易，但是在本發明之中未滿〇. 3 % 的話是可允許。Ni爲未滿0.2%，Ga及V爲均未滿0.1% ，上述以外之不可避免的不純物是由於爲了成形性維持而 應抑制在合計未滿0.3%。 〔再結晶粒徑的平均値爲2 5 v m以下〕 當微細化固溶處理後的再結晶粒時，即使將沖壓加工 度提高且將抽拉高度提高也不會破裂而能成形並提高沖壓 成形性。一旦超過上限値的話效果就降低，另外沖壓後的 質地是無加工至美觀的程度。較佳的再結晶粒尺寸是依次 爲20 /z m以下、15 " m以下。 〔以相當圓徑爲1〜6 // m的金屬間化合物5000個/ mm2 以上〕 以相當圓徑爲1〜6 // m的金屬間化合物係促使冷軋 時的轉位之積體化，具有用來微細化再結晶粒的作用之範 -11 - (8) 1299755 圍的尺寸者，在未滿尺寸及個數的下限値，轉位積體量少 ，其個數在未滿5 000個/ mm2是無法得到較佳的微細再 結晶粒。另外一旦尺寸超過上限値的話粗大化合物在壓延 時成爲條紋或裂損的起點而壓延性降低。另外當上述條件 的化合物狀態時，在連續性地電阻點熔接的情況，藉由銅 製的電極與A1的反應而防止發生熱燒現象，電極的交換 作業次數變少而生產性提高。較佳的化合物數爲6000個 / mm2以上。 接著，說明有關本發明的鋁合金之較佳的製造方法。 熱熔液的熔製是在組成調整後藉由必要之脫氣、沉靜 而施以組成的微調整之同時，以母合金來添加Ti或Ti及 B而鑄造。在鑄造之際，注入熱熔液至相對峙之被強制冷 卻的旋轉帶式鑄模內，以熱熔液的凝固時之冷卻速度40 〜90 °C / sec使之凝固而作成厚度5〜10 mm的厚板，並 從注入熱熔液的相反側拉出該厚板，且直接或從捲筒成渦 狀來壓延。 在連續鑄造方法是具有將熱熔液注入相對峙之被強制 冷卻的旋轉輥軋間，在輥軋面上將熱熔液急冷，從注入熱 熔液的相反側連續性地取出厚度薄的厚板之雙輥軋鑄造法 、或將熱熔液注入相對峙之被強制冷卻的旋轉帶間，在帶 面上將熱熔液急冷，從注入熱熔液的相反側連續性地取出 厚度薄的厚板之雙帶式鑄造法等的方法。 雙輥軋鑄造法是以相當高之凝固時的冷卻速度爲3 0 0 °C / sec以上，所得到的厚板中的化合物尺寸是小的而無 -12- 1299755 Ο) 法得到本發明的板。另一方面’雙帶式鑄造法是在帶面上 將熱熔液急冷是沒有雙輥軋鑄造法那樣高的冷卻速度。 本發明是調節雙帶式鑄造法的鑄造條件而將熱熔液的 冷卻速度設爲40〜90 °C / sec (板厚1/4的位置）而形成 以相當圓徑爲1〜6 // m的金屬間化合物5 000個/ mm2以 上。一旦熱熔液的冷卻速度未滿40 °C / sec的話，晶出粗 大的化合物而不足上述規定尺寸範圍的化合物數，且使再 結晶粒不微細化，無法得到具有優異的沖壓成形性之板。 另外，一*旦超過9〇C / sec的g舌’晶出微細的化合物而不 足規定尺寸範圍的化合物數，並同樣地無法獲得使再結晶 粒微細化之板。 藉由雙帶式鑄造法來將所得到的厚板冷軋而作成所要 的厚度之板，固溶處理並再結晶化。此時，雖然在冷軋的 途中即使退火也可，但是固溶處理所供給的壓延板的壓延 率爲5 5 %以上。固溶處理是以連續退火爐進行。加熱溫 度是以5 00 °C以上，至1〇〇 °C的冷卻速度爲1°C / sec以上 。被固溶處理的壓延板的再結晶粒徑的尺寸，係上述金屬 間化合物的尺寸及個數與該壓延率相輔而可獲得再結晶粒 徑的平均値爲具有2 5 // m以下的再結晶粒之板。如此的 板是就照原樣或爲了得到平坦度而通過1〜5 %左右的表 面輥軋（skin pass)、或整平器（leveler)而被實用地供 給。 〔實施例〕 -13- (10) 1299755 將表1記載的組成之鋁合金熱熔液脫氣沉靜後，在雙 帶式連續鑄造法以熱熔液的冷卻速度50°c / sec及75°C / sec來鑄造了厚度7 mm的厚板。厚板的拉出速度爲8m/ 分鐘。將該厚板冷軋，依其需要中間退火處理，而作成厚 度1 mm的板。接著將該板固溶處理，測定處理後之板的 金屬間化合物尺寸及個數、再結晶粒尺寸' 0.2 %耐力（ YS)、抗拉力（UTS)、拉伸（EL)、圓筒抽拉高度、電 阻點熔接性。顯示結果於表3。 圓筒抽拉條件及電阻點熔接性的評價條件是如下所記 述。 (圓筒抽拉試驗） 使用模具 沖頭（punch) 直徑 5 0mm、 邊倒角R 5 mm、 下模（dies) 內徑 52.5 mm ' 邊倒角R 8 mm、 胚料 直徑 112.5 mm (電阻點熔接性的評價條件） 單相整流式點熔接機 電極 Cu- 1 % Cr合金 加壓力 400kgf 熔接電流値的決定 拉伸剪斷荷重爲滿足以Jis Z3〗40規定的A級平均値之最小的熔接電流値 -14- (11) 1299755 連續打點數 使用已決定之上述的熔接電流値，而 且以上述的熔接條件連續點熔接，連續 A級平均値而超 過的打點數 ◎記號 連續打點數5 00點以上 〇記號 連續打點數200點以上但未滿5 00點 X記號 連續打點數未滿200點Zr is a crystal which promotes the intermetallic compound of Al3Zr, increases the number of recrystallized nuclei by increasing the number of compounds of a specific size, and increases the size of the recrystallized grains to make it more finely recrystallized and improved. Press formability. The effect of the enthalpy is less than the lower limit, and once the upper limit 超过 is exceeded, coarse crystal grains are formed and the rolling property is lowered. [Ti: 0.05% or less, or Ti: 0.05% or less and B: 0.01% or less) • Casting cracks due to rapid cooling during hot melt solidification • 10 - (7) 1299755 虞, Ti or Ti And B is added in order to prevent cracking, Ti: 0.05% or less, or Ti may be added in the above range even in the range of B: 0.01% or less, and in particular, when Ti is compounded, the effect is multiplied. When the effect is visualized, the lower limit Ti of Ti is 0.002% or more, and the lower limit B of B is 0.0005% or more. The unavoidable impurities are those which are mixed from aluminum-based metals, reduced materials, and fusion fixtures, and are represented by Cr, Ni, Zn, Ga, and V. Since Cr is added to prevent stress corrosion cracking of the A1-M-based alloy, it is easy to mix from the reducing material, but it is not sufficient in the present invention. Ni is less than 0.2%, and both Ga and V are less than 0.1%. The unavoidable impurities other than the above are suppressed to a total of less than 0.3% in order to maintain the moldability. [The average enthalpy of the recrystallized grain size is 2 5 vm or less] When the recrystallized grain after the solution treatment is refined, the press forming degree can be improved and the press forming can be improved without increasing the drawing height. Sex. Once the upper limit is exceeded, the effect is reduced, and the texture after stamping is unprocessed to aesthetics. The preferred recrystallized grain size is 20 / z m or less and 15 " m or less. [5000 or more metal compounds with a relative diameter of 1 to 6 // m] The intermetallic compound with a relative diameter of 1 to 6 // m promotes the integration of the index during cold rolling. In the case of the size of the range of -11 - (8) 1299755 used to refine the recrystallized grains, the amount of the indexed product is less than the lower limit of the size and number of the particles, and the number is less than 5,000. The preferred fine recrystallized grains were not obtained in mm/mm2. Further, when the size exceeds the upper limit 粗, the coarse compound becomes a starting point of streaks or cracks at the time of rolling, and the rolling property is lowered. Further, in the case of the compound state under the above conditions, in the case where the resistance point is continuously welded, the reaction between the copper electrode and A1 prevents the occurrence of the hot burning phenomenon, and the number of electrode exchange operations is reduced, and the productivity is improved. The preferred number of compounds is 6,000 / mm 2 or more. Next, a preferred method of producing the aluminum alloy according to the present invention will be described. The melting of the hot melt is carried out by adding Ti, Ti and B to the master alloy while finely adjusting the composition by degassing and calming after the composition adjustment. At the time of casting, the hot melt is injected into a rotating belt type mold which is forcedly cooled relative to the crucible, and is solidified by a cooling rate of 40 to 90 ° C /sec at the time of solidification of the hot melt to a thickness of 5 to 10 mm. The slab is pulled out from the opposite side of the injected hot melt and calendered directly or spirally from the reel. In the continuous casting method, there is a rotary rolling in which the hot melt is injected into the opposite crucible, and the hot melt is quenched on the rolling surface, and the thickness is thinly removed from the opposite side of the hot melt. The double-roll casting method of the plate, or injecting the hot melt into the rotating belt which is forcedly cooled relative to the crucible, quenching the hot melt on the belt surface, and continuously taking out the thin thickness from the opposite side of the injection hot melt A method such as a double-belt casting method for thick plates. The twin-roll casting method is a method in which the cooling rate at a relatively high solidification temperature is 300 ° C /sec or more, and the obtained compound in the thick plate is small in size without -12-1299755 Ο). board. On the other hand, the 'double belt casting method is to cool the hot melt on the belt surface without the high cooling rate as in the twin roll casting method. The present invention is to adjust the casting conditions of the double-belt casting method and set the cooling rate of the hot melt to 40 to 90 ° C / sec (the position of 1/4 of the plate thickness) to form a relatively round diameter of 1 to 6 // The intermetallic compound of m is 5,000 / mm 2 or more. When the cooling rate of the hot melt is less than 40 ° C / sec, the coarse compound is crystallized and the number of the compound is less than the predetermined size range, and the recrystallized grain is not refined, and the sheet having excellent press formability cannot be obtained. . Further, the number of compounds in a predetermined size range is not crystallized by a g tongue of more than 9 〇 C / sec, and a plate which refines the recrystallized grains is not obtained in the same manner. The obtained thick plate was cold-rolled by a double-belt casting method to form a plate having a desired thickness, and was solution-treated and recrystallized. In this case, even if annealing is performed during the cold rolling, the rolling ratio of the rolled sheet supplied by the solution treatment is 55 % or more. The solution treatment is carried out in a continuous annealing furnace. The heating temperature is above 500 °C, and the cooling rate to 1 °C is 1 °C / sec or more. The size of the recrystallized grain size of the calendered sheet to be solution-treated is such that the size and number of the intermetallic compound are complementary to the rolling ratio, and the average enthalpy of the recrystallized grain size is 2 5 // m or less. Recrystallized grain plate. Such a sheet is practically supplied by a skin pass or a leveler of about 1 to 5% as it is or in order to obtain flatness. [Examples] -13- (10) 1299755 After degassing and cooling the aluminum alloy hot melt of the composition shown in Table 1, the cooling rate of the hot melt was 50 ° C / sec and 75 ° in the double belt continuous casting method. C / sec was used to cast thick plates with a thickness of 7 mm. The slab has a pull-out speed of 8 m/min. The thick plate was cold rolled and subjected to intermediate annealing treatment to form a plate having a thickness of 1 mm. Then, the plate was solution-treated, and the size and number of the intermetallic compound of the treated plate, the recrystallized grain size '0.2% of the endurance (YS), the tensile strength (UTS), the tensile (EL), and the cylindrical pumping were measured. Pull height, resistance point fusion. The results are shown in Table 3. The evaluation conditions of the cylindrical drawing condition and the resistance point welding property are as follows. (Cylinder pull test) Use a punch Punch diameter 50 mm, side chamfer R 5 mm, dies inner diameter 52.5 mm 'edge chamfer R 8 mm, billet diameter 112.5 mm (resistance point Evaluation conditions of weldability) Single-phase rectification type spot welding machine electrode Cu-1% Cr alloy plus pressure 400kgf Determination of welding current 拉伸 The tensile shear load is the smallest weld that satisfies the A-class average 规定 specified by Jis Z3 40 Current 値-14- (11) 1299755 The number of continuous taps is determined by the above-mentioned splicing current 値, and continuous welding is performed under the above-mentioned welding conditions, and the average number of consecutive A-level smashes exceeds the number of ticks ◎ mark continuous number of 50,000 points The above 〇 mark consecutively counts more than 200 points but less than 50,000 points X mark continuous number of points is less than 200 points
-15- (12) 1299755 〔表1〕 表1合金組成（單位：質量％ ) 合金編號 Mg Si Fe Mn Cu Zr Ti B 備註 A 0.6 0.8 0.12 0.1 0.02 本發明例 B 0.4 0.8 0.2 0.2 0.02 本發明例 C 0.5 0.7 0.2 0.2 . • 0.02 本發明例 D 0.5 0.8 0.2 0.2 0.01 本發明例 E 0.6 0.8 0.7 0.1 • 0.02 本發明例 F 0.5 0.9 0.15 0.3 0.02 本發明例 G 0.5 0.7 0.2 0.2 0.6 0.02 本發明例 Η 0.5 0.7 0.2 0.2 0.15 0.02 本發明例 I 0.5 0.7 0.2 0.2 0.7 0.12 0.01 本發明例 J L2 0.7 0.2 0.2 0.02 比較例 K 0.5 L4 0.2 0.2 0.02 比較例 L 0.5 0.7 0.05 0.2 0.02 比較例 Μ 0.5 0.7 JL5 0.2 0.02 比較例 N 0.5 0.7 0.2 07 0.02 比較例 0 0.5 0.7 0.2 0.2 L2 0.02 比較例 P 0.5 0.7 0.2 0.2 • 05 0.02 比較例 (註）剩餘部份：A1及其他的不純物 附加下線之値爲本發明的範圍以外。 -16- 1299755 (13) 〔表2〕 表2 製造 契程 試料 合金 鑄造方法/ 冷卻 熱軋 冷軋 中間退火溫 冷軋 固溶處 備註 編號 編號 厚板厚度 速度 (mm) (mm) 度 (mm) 理溫度 (mm) (t/s) ΓΟ/時間(h) (°C) 1 A 雙帶式/7 50 1 550〇c 本發明例 2 B 雙帶式/7 50 1 550〇C 本發明例 3 C 雙帶式/7 50 1 550〇C 本發明例 4 D 雙帶式/7 50 1 550〇C 本發明例 5 E 雙帶式/7 50 1 550〇C 本發明例 6 F 雙帶式/7 50 1 550〇C 本發明例 7 G 雙帶式/7 50 1 550〇C 本發明例 8 Η 雙帶式/7 50 1 550〇C 本發明例 9 I 雙帶式/7 50 1 550〇C 本發明例 10 c 雙帶式/7 50 2.5 360/2 1 550〇C 本發明例 11 B 雙帶式/7 75 1 550〇C 本發明例 12 J 雙帶式/7 50 ] 550〇C 比較例 13 K 雙帶式/7 50 1 550〇C 比較例 14 L 雙帶式/7 50 1 550〇C 比較例 15 M 雙帶式/7 50 1 550〇C 比較例 16 N 雙帶式/7 50 1 550〇C 比較例 17 0 雙帶式/7 50 1 550〇C 比較例 18 P 雙帶式/7 50 1 550〇C 比較例 19 B 雙帶式/20 20 3 1 550〇C 比較例· 20 B 雙帶式/3 150 1 550〇C 比較例 (註）附加下線之値爲本發明的範圍外。 -17- (14) 1299755 〔表3〕 表3 組織及特性 試料 編號 金屬間化合 物的密度 (/mm2) 結晶 粒徑 (μπι) 拉伸特性 圓筒抽 拉高度 (mm) 電阻 點熔 接性 備註 0.2%YS (MPa) UTS (MPa) EL (%) 1 5917 12 130 238 28 14.5 〇 本發明例 2 6812 11 118 222 29 14.1 ◎ 本發明例 3 7185 10 124 228 28 14.3 ◎ 本發明例 4 7726 9 132 239 30 14.7 ◎ 本發明例 5 11254 7 145 249 27 14.2 ◎ 本發明例 6 6917 11 128 235 29 14.8 ◎ 本發明例 7 7435 10 135 264 29 14.9 ◎ 本發明例 8 7982 8 126 230 29 14.8 ◎ 本發明例 9 8013 8 137 266 30 14.9 ◎ 本發明例 10 6725 15 114 219 27 14.0 ◎ 本發明例 11 7820 9 122 230 30 15.1 ◎ 本發明例 12 7543 11 140 252 24 13.5 ◎ 比較例 13 7521 9 131 251 23 13.6 ◎ 比較例 14 3924 26 112 215 26 13.5 X 比較例 15 36721 6 133 241 21 13.5 ◎ 比較例 16 7820 11 134 248 20 13.7 ◎ 比較例 17 7541 9 160 288 22 13.8 ◎ 比較例 18 8783 7 142 235 21 13.9 ◎ 比較例 19 2215 29 109 215 20 12.5 X 比較例 20 3272 26 113 218 22 12.8 X 比較例 (註） ◎記號 連續打點數500點以上 〇記號 連續打點數200點以上但未滿5 00點 X記號 連續打點數未滿200點 附加下線之値爲本發明的範圍外。 再結晶粒徑是以橫切（ crosscut )法來測定。 -18- (15) 1299755 從表1〜3的結果，判明本發明的實施例（試料號碼 1〜11)是圓筒抽拉高度高而具有優異的沖壓成形性，另 外連續打點數多就具有優異的連續電阻點熔接性。另_方 面，判明從組成爲本發明的範圍外的比較例（試料號碼 1 2〜1 8 )，係圓筒抽拉高度爲低而具有差的沖壓成形性， 另外相當圓徑爲1〜6 // m的金屬間化合物少而結晶粒徑 大的比較例（試料號碼1 4、1 9、20 )，係連續打點數少 就具有差的連續電阻點熔接性。 〔產業上之可利用性〕 如以上所述，本發明的鋁合金板是因爲具有優異的沖 壓成形性及連續電阻點熔接性，所以沖壓成形體的質地是 加工至美觀的程度，另外因爲由於電阻點熔接的組裝能連 續，所以生產性優異，從6000系的合金板以施予塗裝等 之後的熱燒處理就使強度提高等，例如能廣範圍大幅地使 用在汽車的車體薄板等的用途等之具有優異的工業性價値 -19--15- (12) 1299755 [Table 1] Table 1 Alloy composition (unit: mass%) Alloy No. Mg Si Fe Mn Cu Zr Ti B Remark A 0.6 0.8 0.12 0.1 0.02 Inventive Example B 0.4 0.8 0.2 0.2 0.02 Inventive Example C 0.5 0.7 0.2 0.2 . • 0.02 Inventive Example D 0.5 0.8 0.2 0.2 0.01 Inventive Example E 0.6 0.8 0.7 0.1 • 0.02 Inventive Example F 0.5 0.9 0.15 0.3 0.02 Inventive Example G 0.5 0.7 0.2 0.2 0.6 0.02 Inventive Example Η 0.5 0.7 0.2 0.2 0.15 0.02 Inventive Example I 0.5 0.7 0.2 0.2 0.7 0.12 0.01 Inventive Example J L2 0.7 0.2 0.2 0.02 Comparative Example K 0.5 L4 0.2 0.2 0.02 Comparative Example L 0.5 0.7 0.05 0.2 0.02 Comparative Example Μ 0.5 0.7 JL5 0.2 0.02 Comparative Example N 0.5 0.7 0.2 07 0.02 Comparative Example 0 0.5 0.7 0.2 0.2 L2 0.02 Comparative Example P 0.5 0.7 0.2 0.2 • 05 0.02 Comparative Example (Note) Remaining portion: A1 and other impurities are added to the lower line and are the scope of the present invention. other than. -16- 1299755 (13) [Table 2] Table 2 Manufacturing process sample alloy casting method / Cooling hot rolling cold rolling intermediate annealing temperature cold rolling solid solution place Remarks No. Thick plate thickness speed (mm) (mm) Degree (mm Temperature (mm) (t/s) ΓΟ/time (h) (°C) 1 A double belt type / 7 50 1 550 〇 c Inventive example 2 B double belt type / 7 50 1 550 〇 C The present invention Example 3 C Double belt type / 7 50 1 550 〇 C Inventive Example 4 D Double belt type / 7 50 1 550 〇 C Inventive Example 5 E Double belt type / 7 50 1 550 〇 C Inventive Example 6 F Double belt Formula / 7 50 1 550 〇 C Inventive Example 7 G Double belt type / 7 50 1 550 〇 C Inventive Example 8 Η Double belt type / 7 50 1 550 〇 C Inventive Example 9 I Double belt type / 7 50 1 550 〇 C Inventive Example 10 c Double belt type / 7 50 2.5 360/2 1 550 〇 C Inventive Example 11 B Double belt type / 7 75 1 550 〇 C Inventive Example 12 J Double belt type / 7 50 ] 550 〇C Comparative Example 13 K Double belt type / 7 50 1 550 〇 C Comparative Example 14 L Double belt type / 7 50 1 550 〇 C Comparative Example 15 M Double belt type / 7 50 1 550 〇 C Comparative Example 16 N Double belt Equation /7 50 1 550〇C Comparative Example 17 0 Double belt / 7 50 1 550 〇C Comparative Example 18 P Double belt type / 7 50 1 550 〇 C Comparative Example 19 B Double belt type / 20 20 3 1 550 〇 C Comparative example · 20 B Double belt type / 3 150 1 550 〇 C Comparative example (Note) The addition of the offline is outside the scope of the present invention. -17- (14) 1299755 [Table 3] Table 3 Structure and characteristics Sample number Density of intermetallic compound (/mm2) Crystal grain size (μπι) Tensile characteristics Cylinder drawing height (mm) Resistance point weldability Remarks 0.2 %YS (MPa) UTS (MPa) EL (%) 1 5917 12 130 238 28 14.5 〇 Inventive Example 2 6812 11 118 222 29 14.1 ◎ Inventive Example 3 7185 10 124 228 28 14.3 ◎ Inventive Example 4 7726 9 132 239 30 14.7 ◎ Inventive Example 5 11254 7 145 249 27 14.2 ◎ Inventive Example 6 6917 11 128 235 29 14.8 ◎ Inventive Example 7 7435 10 135 264 29 14.9 ◎ Inventive Example 8 7982 8 126 230 29 14.8 ◎ The present invention Example 9 8013 8 137 266 30 14.9 ◎ Inventive Example 10 6725 15 114 219 27 14.0 ◎ Inventive Example 11 7820 9 122 230 30 15.1 ◎ Inventive Example 12 7543 11 140 252 24 13.5 ◎ Comparative Example 13 7521 9 131 251 23 13.6 ◎ Comparative Example 14 3924 26 112 215 26 13.5 X Comparative Example 15 36721 6 133 241 21 13.5 ◎ Comparative Example 16 7820 11 134 248 20 13.7 ◎ Comparative Example 17 7541 9 160 288 22 13.8 ◎ Comparative Example 18 8783 7 142 235 21 13.9 ◎ Comparative Example 19 2215 29 109 215 20 12.5 X Comparative Example 20 3272 26 113 218 22 12.8 X Comparative example (Note) ◎ Mark continuous number of hits of 500 points or more 〇 Mark continuous number of hits of 200 points or more but less than 50,000 points X mark continuous number of hits is not full The addition of 200 points to the offline is outside the scope of the present invention. The recrystallized particle diameter is measured by a crosscut method. -18- (15) 1299755 From the results of Tables 1 to 3, it was found that the examples (sample numbers 1 to 11) of the present invention have high cylinder drawing height and excellent press formability, and have a large number of continuous dots. Excellent continuous resistance point fusion. On the other hand, it is found that the comparative example (sample No. 1 2 to 18) which is outside the scope of the present invention has a low drawing height and a poor press formability, and the equivalent circular diameter is 1 to 6 In the comparative example (sample number 14, 19, 20) in which the number of intermetallic compounds is small and the crystal grain size is large, the continuous resistance point fusion property is poor when the number of continuous dots is small. [Industrial Applicability] As described above, the aluminum alloy sheet of the present invention has excellent press formability and continuous resistance spot weldability, so that the texture of the press-formed body is processed to an aesthetic level, and because Since the assembly of the resistance point welding can be continued, the productivity is excellent, and the strength of the 6000-series alloy sheet after the application of the coating or the like is improved, and the strength can be improved, for example, in a wide range of automobile body sheets. The use of such an excellent industrial price 値-19-