TWI355301B - Aluminum alloy thick plate and method for manufact - Google Patents

Description

1355301 壓延板之特性。 較佳者係前述之鋁合金厚板的製造方法，其中前述平 滑化處理步驟係藉由切削法、硏削法、及硏磨法中任何一 種以上的方法進行。 藉由該法，可形成鋁合金厚板之板厚精度及平坦性良 好者。而且，可抑制因瑕疵或黑線條等之表面缺陷。 [發明效果] 藉由發明之鋁合金厚板，於塑性變形少的厚板中，由 於形成企求的板厚及平坦的厚板，故適合於製作要求正確 形狀之半導體相關裝置等。而且，由於可抑制因瑕疵或黑 線條等之表面缺陷’故可形成厚板之表面性質良好者。此 外’藉由使用所定的鋁合金，可提高強度等之特性，且可 抑制表面產生色斑情形，形成厚板之表面性質更佳者。 藉由本發明之銘合金厚板之製造方法，可以良好的生 產性製造具有前述效果之鋁合金厚板。 [爲實施發明之最佳形態] 於下述中，說明有關爲實現本發明之鋁合金厚板時的 最佳形態。 [鋁合金厚板之構成] 本發明之鋁合金厚板，係爲使表面平滑化的鋁合金熱 間壓延板（鋁合金熱延板），表面之平坦度在每lm之壓延 -11 - 1355301 方向長度爲0.2mm以下，板厚之不均勻性在企求的板厚 ±0.5 %以內。而且，本發明之鋁合金厚板，係板厚爲〗5〜 2 0 0mm之板材，沒有特別的限制，可視鋁合金板厚之用途 而定予以適當改變。於下述中，說明有關構成本發明之鋁 合金厚板的各要素。 (表面之平坦度：在每lm之壓延方向長度爲0.2mm以下） 半導體相關裝置之構件，特別是如電漿處理裝置之真 空裝置用室的內部構件中使用平坦性不佳的構件時，於高 真空中減壓時，藉由自構件表面放出吸附氣體，可降低真 空度。因此，達到目標之真空度爲止需要時間，且生產效 率降低。然而，本發明之鋁合金厚板的表面平坦度，係爲 0.2 mm/m以下。而且，熱間壓延板之表面平坦性，由於壓 延方向最爲不佳，故爲每lm壓延方向長度。該平坦性係藉 由下述之製造方法中平滑化處理步驟及矯正步驟予以調整 (板厚之不均勻性：企求板厚之±0.5 %以內） 本發明之鋁合金厚度，爲製作半導體相關裝置之構件 等、要求形狀爲高精度的製品時，亦要求板厚爲高精度。 爲對應於該要求時，板厚之不均勻性在企求板厚之±0.5% 以內。該板厚精度係藉由下述之製造方法中平滑化處理步 驟予以調整。 此外’本發明之鋁合金厚板，以每100g中含有的氫氣 -12- 1355301 量爲0_2ml以下較佳，以0.1 ml以下更佳。氫氣係自附著於 燃料中之氫氣或金塊等之水分、其他的有機物等產生。含 有多量氫氣時，係爲形成針孔的原因，且製品之強度變弱 。而且，在鑄塊表面附近之粒界上集聚氫氣且濃化，產生 鑄塊之碎片（blister )、及來自碎片的鋁合金厚板的剝離 (peeling)情形，同時作爲厚板之表面缺陷所呈現的厚板 表面板之潛在缺陷。此外，在真空裝置用室之內部構件上 有此等之缺陷時，在高真空中減壓時，藉由使構件上固熔 的氣體原子放出於表面，可降低真空度。因此，達到目標 之真空度爲止之時間耗時，生產效率降低。爲減低鋁合金 厚板中所含的氫氣量時，在下述製造方法中之脫氫步驟中 ，自鑄造前之鋁合金熔湯除去氫氣。 鑄塊之氫氣濃度，例如可自鑄塊（均熱處理前）切取 試樣’以醇及丙酮進行超音波洗淨處理後，藉由惰性氣體 氣流溶解熱傳導度法（LIS ( Light-Metal Indusrial Standard) A06-1 993 )求取。而且，鋁合金厚板之氫氣濃 度’例如可自鋁合金厚板切取試樣，浸漬於NaOH後，以 硝酸除去表面之氧化皮膜，以醇與丙酮進行超音波洗淨後 ’藉由真空加熱萃取容量法（LISA06-1993)求取。 本發明之鋁合金厚板，亦可爲由任意的鋁合金所形成 者’選自Al-Mg系合金、Al-Mn系合金、Al-Mg-Si系合金、 Al-Zn-Mg系合金中任何—種，適合其用途之材料。於下述 中’說明有關構成本發明之鋁合金厚板之鋁合金例的各要 素。 -13- 1355301 [Al-Mg系合金之組成] 本發明之Al-Mg系合金、即以5000系A1合金爲基準之 鋁合金，由含有Mg: 1.5〜12.0質量％、及含有〗種以上之 Si : 0.7質量％以下、Fe : 0.8質量％以下、Cu : 0.6質量％以 下、Μη: 1.0質量％以下、Cr: 0.5質量％以下、Zn: 0.4質 量％以下、Ti : 0.1質量％以下，且殘留成分爲A1及不可避 免的雜質所形成。 (M g : 1 _ 5 〜1 2.0 質量 ％ )1355301 Characteristics of rolled sheets. Preferably, the method for producing an aluminum alloy thick plate described above is carried out, wherein the smoothing treatment step is carried out by any one of a cutting method, a boring method, and a honing method. By this method, it is possible to form a plate thickness precision and flatness of an aluminum alloy thick plate. Moreover, surface defects such as flaws or black lines can be suppressed. [Effect of the Invention] In the thick aluminum plate of the invention, it is suitable for producing a semiconductor-related device requiring a correct shape because a plate thickness and a flat thick plate are formed in a thick plate having a small plastic deformation. Further, since surface defects such as defects or black lines can be suppressed, the surface properties of the thick plate can be formed to be good. Further, by using a predetermined aluminum alloy, characteristics such as strength can be improved, and staining on the surface can be suppressed, and the surface properties of the thick plate can be improved. According to the method for producing a thick alloy plate of the present invention, an aluminum alloy thick plate having the aforementioned effects can be produced with good productivity. [Best Mode for Carrying Out the Invention] In the following, the best mode for realizing the aluminum alloy thick plate of the present invention will be described. [Composition of Aluminum Alloy Thick Plate] The aluminum alloy thick plate of the present invention is an aluminum alloy hot-rolled sheet (aluminum alloy heat-expanded plate) for smoothing the surface, and the flatness of the surface is rolled at lm - 113551 The length of the direction is 0.2 mm or less, and the unevenness of the sheet thickness is within ±0.5% of the desired sheet thickness. Further, the aluminum alloy thick plate of the present invention is a plate having a thickness of from 5,000 to 2,000 mm, and is not particularly limited, and may be appropriately changed depending on the use of the thickness of the aluminum alloy plate. Hereinafter, each element constituting the aluminum alloy thick plate of the present invention will be described. (Flatness of surface: 0.2 mm or less in the rolling direction per lm) When a member of a semiconductor-related device is used, particularly when a member having a poor flatness is used for an internal member of a chamber for a vacuum device such as a plasma processing device, When depressurizing in a high vacuum, the degree of vacuum can be lowered by releasing the adsorbed gas from the surface of the member. Therefore, it takes time to reach the target degree of vacuum, and the production efficiency is lowered. However, the aluminum alloy thick plate of the present invention has a surface flatness of 0.2 mm/m or less. Moreover, the surface flatness of the hot rolled sheet is the length of the rolling direction per lm because the direction of the rolling is the most unsatisfactory. The flatness is adjusted by the smoothing process step and the correcting step in the following manufacturing method (non-uniformity of the sheet thickness: within ±0.5% of the sheet thickness). The thickness of the aluminum alloy of the present invention is for fabricating a semiconductor related device. When a member such as a member is required to have a high-precision shape, the thickness of the plate is also required to be high. In order to cope with this requirement, the unevenness of the sheet thickness is within ±0.5% of the sheet thickness. The plate thickness accuracy is adjusted by the smoothing process in the manufacturing method described below. Further, the aluminum alloy thick plate of the present invention preferably has a hydrogen content of -12 to 1355301 per 100 g of 0-2 ml or less, more preferably 0.1 ml or less. The hydrogen gas is generated from moisture such as hydrogen gas or gold nuggets attached to the fuel, other organic substances, and the like. When a large amount of hydrogen is contained, it is a cause of pinhole formation, and the strength of the product becomes weak. Moreover, hydrogen is concentrated and concentrated on the grain boundary near the surface of the ingot to produce blister of the ingot and peeling of the aluminum alloy slab from the chip, and at the same time as a surface defect of the slab Potential defects in the slab surface plate. Further, when such a defect is present in the internal member of the vacuum chamber, when the pressure is reduced under high vacuum, the degree of vacuum can be lowered by releasing the gas atoms solidified on the member to the surface. Therefore, the time until the target vacuum is reached is time-consuming, and the production efficiency is lowered. In order to reduce the amount of hydrogen contained in the aluminum alloy thick plate, in the dehydrogenation step in the following production method, hydrogen gas is removed from the aluminum alloy melt before casting. The hydrogen concentration of the ingot can be, for example, cut from the ingot (before the soaking treatment). After ultrasonic cleaning with alcohol and acetone, the heat conductivity method (LIS (Light-Metal Indusrial Standard) is used. A06-1 993) Seek. Moreover, the hydrogen concentration of the aluminum alloy thick plate can be cut from the aluminum alloy thick plate, for example, after immersing in NaOH, the surface oxide film is removed with nitric acid, ultrasonically washed with alcohol and acetone, and then extracted by vacuum heating. The capacity method (LISA06-1993) is obtained. The aluminum alloy thick plate of the present invention may be formed of any aluminum alloy selected from the group consisting of an Al-Mg alloy, an Al-Mn alloy, an Al-Mg-Si alloy, and an Al-Zn-Mg alloy. Any kind of material suitable for its use. Each of the elements of the aluminum alloy constituting the aluminum alloy thick plate of the present invention will be described below. -13- 1355301 [Composition of Al-Mg-based alloy] The Al-Mg-based alloy of the present invention, that is, an aluminum alloy based on a 5000-series A1 alloy, contains Mg: 1.5 to 12.0% by mass, and contains the above-mentioned species. Si: 0.7% by mass or less, Fe: 0.8% by mass or less, Cu: 0.6% by mass or less, Μη: 1.0% by mass or less, Cr: 0.5% by mass or less, Zn: 0.4% by mass or less, and Ti: 0.1% by mass or less; The residual component is formed by A1 and unavoidable impurities. (M g : 1 _ 5 〜 1 2.0 mass % )

Mg係具有提高Al-Mg系合金之強度。Mg之含量未達 1 .5質量％時，其效果小，另外，Mg之含量大於12.0質量％ 時，鑄造性顯著降低，且無法製造製品。因此，使用前述 成分組成之Al-Mg系合金時’ Mg之含量必須爲12.0質量％ 。因此，Mg之含量爲1.5〜12.0質量％。 (Si : 0.7質量％以下）The Mg system has an increased strength of the Al-Mg alloy. When the content of Mg is less than 1.5% by mass, the effect is small, and when the content of Mg is more than 12.0% by mass, the castability is remarkably lowered, and the product cannot be produced. Therefore, when the Al-Mg-based alloy having the above composition is used, the content of Mg must be 12.0% by mass. Therefore, the content of Mg is 1.5 to 12.0% by mass. (Si: 0.7% by mass or less)

Si係爲於鋁合金中作爲原料雜質無法避免所含有的元 素。Si雖具有提高鋁合金之強度效果，另外，於鑄造時等 ，與Mn、Fe鍵結，產生Al-(Fe) - (Mn) -Si系金屬間化 合物。Si含量大於0.7質量％時，在鑄塊容易產生粗大的金 屬間化合物，於耐酸鋁處理後表面外觀容易產生色斑。因 此，Si之含量爲0.7質量％以下。 1355301 (Fe : 0.8質量％以下）The Si system is an element that cannot be avoided as a raw material impurity in an aluminum alloy. Si has an effect of improving the strength of the aluminum alloy, and is bonded to Mn and Fe at the time of casting to form an Al-(Fe) - (Mn) -Si-based intermetallic compound. When the Si content is more than 0.7% by mass, a coarse intermetallic compound is likely to be formed in the ingot, and the surface appearance is likely to cause stains after the alumite treatment. Therefore, the content of Si is 0.7% by mass or less. 1355301 (Fe: 0.8% by mass or less)

Fe係爲於鋁合金中作爲原料雜質無法避免所含有的元 素。Fe具有使鋁合金之結晶粒予以微細化、安定化，且提 高強度的效果。另外，於鑄造時等，與Mn、Si鍵結，產生 Al-Fe- ( Mn) - ( Si)系金屬間化合物》Fe含量大於0·8質 量％時，在鑄塊容易產生粗大的金屬間化合物，於耐酸鋁 處理後表面外觀容易產生色斑。因此，Fe之含量爲0.8質 量％以下。 (Cu : 0.6質量％以下）Fe is an element that cannot be avoided as a raw material impurity in an aluminum alloy. Fe has an effect of making the crystal grains of the aluminum alloy finer and more stable and improving the strength. In addition, when Mn or Si is bonded during casting, an Al-Fe-(Mn)-(Si)-based intermetallic compound is produced, and when the Fe content is more than 0.8% by mass, the ingot is likely to be coarse between the metals. The surface of the compound is easily stained after the alumite treatment. Therefore, the content of Fe is 0.8% by mass or less. (Cu: 0.6% by mass or less)

Cu係具有在鋁合金中固熔，提高強度的效果。以Cu之 含量爲0.6質量時％，可充分確保作爲Al-Mg系合金使用時 之強度，即使添加超過該量時，效果飽和。因此，Cu之含 量爲0.6質量％以下。 (Mn : 1 .〇質量％以下） Μη係具有在鋁合金中固熔，提高強度的效果。另外， Μη含量大於1.〇質量％時，在鑄塊容易產生粗大的金屬間 化合物，於耐酸鋁處理後表面外觀容易產生色斑。因此， Μη之含量爲1.〇質量％以下。 (Cr : 0.5質量％以下）The Cu system has an effect of solid-melting in an aluminum alloy to improve strength. When the content of Cu is 0.6% by mass, the strength when used as an Al-Mg-based alloy can be sufficiently ensured, and even when the amount exceeds this amount, the effect is saturated. Therefore, the content of Cu is 0.6% by mass or less. (Mn : 1 .〇% by mass or less) The Μη system has an effect of solid-melting in an aluminum alloy to improve strength. Further, when the Μη content is more than 1. 〇% by mass, a coarse intermetallic compound is likely to be formed in the ingot, and the surface appearance is likely to cause stains after the alumite treatment. Therefore, the content of Μη is 1. 〇 mass% or less. (Cr: 0.5% by mass or less)

Cr係於鑄造時或熱處理時析出作爲微細的化合物，具 有抑制結晶粒成長的效果。Cr之含量大於0.5質量％時，產 -15- 1355301 生粗大的Al-Cr系金屬間化合物作爲初晶，於耐酸鋁處理 後表面外觀容易產生色斑。因此，Cr之含量爲0.5質量％以 下。 (Zn : 0.4質量％以下）Cr is precipitated as a fine compound during casting or heat treatment, and has an effect of suppressing the growth of crystal grains. When the content of Cr is more than 0.5% by mass, a coarse Al-Cr-based intermetallic compound of -15 to 1355301 is produced as a primary crystal, and the surface of the surface is likely to be colored after the alumite treatment. Therefore, the content of Cr is 0.5% by mass or less. (Zn: 0.4% by mass or less)

Zn雖具有提高鋁合金之強度的效果，另外，Zn之含量 爲0.4質量％時，可充分確保作爲Al-Mg系合金之強度，即 使添加大於該値時，效果仍飽和。因此，Zn含量爲0.4質 量％以下。 (Ti : 0_1質量％以下）Zn has an effect of improving the strength of the aluminum alloy, and when the content of Zn is 0.4% by mass, the strength of the Al-Mg-based alloy can be sufficiently ensured, and even when the addition is larger than the ruthenium, the effect is saturated. Therefore, the Zn content is 0.4% by mass or less. (Ti : 0_1 mass% or less)

Ti係具有使鋁合金之微晶粒予以微細化的效果。即使 Ti之含量大於0.1質量％時，其效果仍飽和。然而，Ti之含 量爲0.1質量％以下。 [Al-Mn系合金之組成] 其次，說明有關A1-Μη系合金之各要素。本發明之A1-Μη系合金、即以3 000系Α1合金爲基準之鋁合金，由含有 Μη : 0.3〜1.6質量％、及含有1種以上之Si : 0.7質量％以下 、Fe : 〇.8質量％以下、Cu : 0.5質量％以下、Mg : 1.5質量 %以下、Cr : 0.3質量％以下、Zn : 0.4質量％以下、Ti : 1 質量％以下，且殘留成分爲A1及不可避免的雜質所形成。 (Μη: 〇_3 〜1.6質量％) -16- 1355301 Μη係在鋁合金中固熔，提高強度之效果。Μη之含量 未達0.3質量％時，其效果小，另外，Μη之含量大於1.6質 量％時，在鑄塊中產生粗大的Al- ( Fe ) -Mn- ( Si )系金屬 間化合物，耐酸鋁處理後之表面外觀容易產生色斑。因此 ，Μη之含量爲0.3〜1.6質量％。 (Mg : 1.5質量％以下）The Ti system has an effect of refining fine crystal grains of an aluminum alloy. Even if the content of Ti is more than 0.1% by mass, the effect is saturated. However, the content of Ti is 0.1% by mass or less. [Composition of Al-Mn Alloy] Next, each element of the A1-Μη alloy will be described. The A1-Μη alloy of the present invention, that is, the aluminum alloy based on the 3,000 Α1 alloy, contains Μη: 0.3 to 1.6% by mass, and one or more kinds of Si: 0.7% by mass or less, Fe: 〇.8 Mass% or less, Cu: 0.5% by mass or less, Mg: 1.5% by mass or less, Cr: 0.3% by mass or less, Zn: 0.4% by mass or less, Ti: 1% by mass or less, and the residual component is A1 and unavoidable impurities form. (Μη: 〇_3 to 1.6% by mass) -16- 1355301 Μη is solid-melted in an aluminum alloy to improve the strength. When the content of Μη is less than 0.3% by mass, the effect is small, and when the content of Μη is more than 1.6% by mass, coarse Al-(Fe)-Mn-(Si)-based intermetallic compound is produced in the ingot, and the acid-resistant aluminum is produced. The surface appearance after the treatment is liable to cause stains. Therefore, the content of Μη is 0.3 to 1.6% by mass. (Mg: 1.5% by mass or less)

Mg係具有提高鋁合金之強度的效果。Mg之含量爲1.5 質量％時，充分確保使用作爲Al-Μη系合金厚板時之強度 ，即使添加大於該値時，效果飽和。因此，Mg之含量爲 1.5質量％以下。 (Si : 0_7質量％以下、Fe : 〇.8質量％以下、Cu : 0.5質量％ 以下、C r : 0 · 3質量％以下、Ζ η : 0.4質量％以下、Ti : 0 · 1 質量％以下）The Mg system has an effect of increasing the strength of the aluminum alloy. When the content of Mg is 1.5% by mass, the strength when using a thick plate of an Al-Μη alloy is sufficiently ensured, and even when the addition is larger than the enthalpy, the effect is saturated. Therefore, the content of Mg is 1.5% by mass or less. (Si: 0_7 mass% or less, Fe: 〇.8 mass% or less, Cu: 0.5 mass% or less, Cr: 0 · 3 mass% or less, Ζ η: 0.4 mass% or less, and Ti: 0 · 1 mass% or less )

Si、Fe、Cu、Cr、Zn、Ti之各效果’與Al-Mg系合金 者相同，故省略。 [Al-Mg-Si系合金之組成] 其次，說明有關A1_MS-Si系合金之各要素。本發明之 Al-Mg-Si系合金、即以6000系AI合金爲基準之鋁合金，由 含有Mg: 0.3〜1.5質量％、及Si: 0.2〜1.6質量％以下、且 含有1種以上之F e : 〇 . 8質量％以下、C u : 1 · 0質量°/。以下' Μη : 0.6質量％以下、Cr : 0.5質量％以下、Zn : 0.4質量％ -17- 1355301 以下、Ti: 0.1質量％以下，且殘留成分爲A1及不可避免的 雜質所形成。 (Mg: 0.3〜1.5 質量 ％)The respective effects of Si, Fe, Cu, Cr, Zn, and Ti are the same as those of the Al-Mg-based alloy, and therefore are omitted. [Composition of Al-Mg-Si Alloy] Next, each element of the A1_MS-Si alloy will be described. The Al-Mg-Si-based alloy of the present invention, that is, the aluminum alloy based on the 6000-series AI alloy, contains Mg: 0.3 to 1.5% by mass, and Si: 0.2 to 1.6% by mass or less, and contains one or more types of F. e : 〇. 8 mass% or less, C u : 1 · 0 mass °/. Hereinafter, 'Μη: 0.6% by mass or less, Cr: 0.5% by mass or less, Zn: 0.4% by mass -17 to 1355301 or less, and Ti: 0.1% by mass or less, and the residual component is A1 and an unavoidable impurity. (Mg: 0.3~1.5 mass %)

Mg係提高鋁合金之強度的效果，另外’藉由與Si共存 ，形成M g2 Si，提高鋁合金之強度。Mg之含量未達0.3質量 %時，此等之效果小，另外，Mg之含量大於1.5質量％時’ 形成Al-Mg系（ 5000系A1)合金之特性。因此，Mg之含量 爲0.3〜1 · 5質量％。 (S i : 〇 · 2 〜1 . 6 質量 ％ )The effect of Mg is to increase the strength of the aluminum alloy, and the strength of the aluminum alloy is improved by coexistence with Si to form Mg 2 Si. When the content of Mg is less than 0.3% by mass, the effect of these is small, and when the content of Mg is more than 1.5% by mass, the characteristics of the Al-Mg-based (5000-based A1) alloy are formed. Therefore, the content of Mg is 0.3 to 1.5% by mass. (S i : 〇 · 2 ~ 1. 6 mass % )

Si係具有提高鋁合金之強度的效果’另外’藉由與Mg 共存時，形成Mg2Si，提高鋁合金之強度。Si含量未達0.2 質量％時，此等之效果小。另外，S i之含量大於1 · 6質量％ 時，在Al-Mg-Si系合金中產生粗大的金屬間化合物，於耐 酸鋁處理後表面外觀容易產生色斑。因此’ Si之含量爲0.2 〜1.6質量％。 (Cu : 1.0質量％以下）The Si system has an effect of improving the strength of the aluminum alloy. In addition, when coexisting with Mg, Mg2Si is formed to increase the strength of the aluminum alloy. When the Si content is less than 0.2% by mass, the effects are small. Further, when the content of Si is more than 1.6 mass%, a coarse intermetallic compound is formed in the Al-Mg-Si-based alloy, and the surface appearance is likely to cause stains after the alumite treatment. Therefore, the content of Si is 0.2 to 1.6% by mass. (Cu : 1.0% by mass or less)

Cu係固熔於在鋁合金中，具有提高強度的效果，此外 ，Cu之含量大於1.0質量％時，Al-Mg-Si系合金之耐腐蝕性 降低。因此，Cu含量爲1.〇質量％以下。 (Zn : 0.4質量％以下） -18- 1355301Cu is solid-melted in an aluminum alloy and has an effect of improving strength. When the content of Cu is more than 1.0% by mass, the corrosion resistance of the Al-Mg-Si alloy is lowered. Therefore, the Cu content is 1. 〇 mass% or less. (Zn: 0.4% by mass or less) -18- 1355301

Zn具有提高鋁合金之強度的效果。另外，Zn之含量大 於0.4質量％時，Al-Mg-Si系合金之耐腐蝕性降低。因此’ Zn之含量爲0.4質量％以下。 (Fe: 0.8質量％以下、Μη: 0.6質量％以下、Cr: 0.5質量 %以下、Ti : 0.1質量°/。以下）Zn has the effect of increasing the strength of the aluminum alloy. Further, when the content of Zn is more than 0.4% by mass, the corrosion resistance of the Al-Mg-Si-based alloy is lowered. Therefore, the content of Zn is 0.4% by mass or less. (Fe: 0.8% by mass or less, Μη: 0.6% by mass or less, Cr: 0.5% by mass or less, and Ti: 0.1% by mass or less)

Fe、Mn、Cr、Ti之各效果，由於與Al-Mg系合金者相 t 同，故予以省略。 [Al-Zn-Mg系合金之組成] 其次，說明有關Al-Zn-Mg系合金之各要素。本發明之 Al-An-Mg系合金、即以7000系A1合金爲基準之鋁合金，係 由含有Zn: 3.0〜9.0質量％、Mg: 0.4〜4.0質量％、及含有 1種以上之S i : 0.7質量％以下、F e : 0.8質量％以下、C u : 3.0質量％以下、Μη : 0.8質量％以下' Cr : 0.5質量％以下 >、Ti: 0.1質量％以下' Zr: 0.25質量％以下，且殘留成分 爲A1及不可避免的雜質所形成的鋁合金所形成。 (Zn : 3.0 〜9.0質量 ％)The effects of Fe, Mn, Cr, and Ti are omitted since they are the same as those of the Al-Mg-based alloy. [Composition of Al-Zn-Mg-Based Alloy] Next, each element of the Al-Zn-Mg-based alloy will be described. The Al-An-Mg-based alloy of the present invention, that is, the aluminum alloy based on the 7000-based Al alloy, contains Zn: 3.0 to 9.0% by mass, Mg: 0.4 to 4.0% by mass, and one or more kinds of S i : 0.7% by mass or less, F e : 0.8% by mass or less, C u : 3.0% by mass or less, Μη: 0.8% by mass or less 'Cr : 0.5% by mass or less>, Ti: 0.1% by mass or less 'Zr: 0.25 % by mass Hereinafter, an aluminum alloy having a residual component of A1 and unavoidable impurities is formed. (Zn: 3.0 to 9.0 mass%)

Zn雖具有提高鋁合金之強度的效果。Zn之含量未達 3.0質量％時，該效果小，另外，Zn之含量大於9.0質量％時 ，產生粗大的金屬間化合物，耐酸鋁處理厚之表面外觀不 容易產生色斑’且會使耐SCC (耐應力腐蝕破裂）性降低 。因此，Zn之含量爲3.0〜9.0質量％。 1355301 (Mg: 0.4 〜4.0 質量 ％)Zn has the effect of increasing the strength of the aluminum alloy. When the content of Zn is less than 3.0% by mass, the effect is small, and when the content of Zn is more than 9.0% by mass, a coarse intermetallic compound is produced, and the surface of the alumite treatment is not likely to cause stains and the SCC is resistant. (Resistance to stress corrosion cracking) is reduced. Therefore, the content of Zn is 3.0 to 9.0% by mass. 1355301 (Mg: 0.4 to 4.0 mass %)

Mg具有提高鋁合金之強度的效果。Mg之含量未達0.4 質量％，該效果小，另外’ Mg之含量大於4.0質量％時’容 易產生粗大的金屬化合物，耐酸鋁處理後之表面外觀容易 產生色斑，會降低耐SCC (耐應力腐蝕破裂）性。因此’ Mg之含量爲0.4〜4.0質量°/〇。 (Cu : 3.0質量％以下）Mg has an effect of increasing the strength of the aluminum alloy. The content of Mg is less than 0.4% by mass, and the effect is small. When the content of Mg is more than 4.0% by mass, it is easy to produce a coarse metal compound, and the surface appearance after the alumite treatment is liable to cause stains, which may lower the resistance to SCC (stress resistance). Corrosion cracking). Therefore, the content of 'Mg is 0.4 to 4.0 mass%/〇. (Cu: 3.0% by mass or less)

Cu係固熔於在鋁合金中，具有提高強度的效果，此外 ，Cu之含量大於3.0質量％時，Al-Zn-Mg系合金之耐腐蝕性 降低。因此，Cu含量爲3.0質量％以下。 (Zr : 0.25質量％以下）Cu is solid-melted in an aluminum alloy and has an effect of improving strength. When the content of Cu is more than 3.0% by mass, the corrosion resistance of the Al-Zn-Mg-based alloy is lowered. Therefore, the Cu content is 3.0% by mass or less. (Zr : 0.25 mass% or less)

Zr具有使錫合金之結晶粒予以微細化、且安定化的效 果。另外，Zr之含量大於0.25質量％時，容易產生粗大的 金屬間化合物，且耐酸錦處理後之表面外觀容易產生色斑 。因此’ Zr之含量爲0.25質量％以下。 (Si: 0.7質量％以下、Fe: 0.8質量％以下、Μη: 〇.8質量 %以下、Cu : 0.5質量％以下、Ti : 0.1質量％以下）Zr has an effect of making the crystal grains of the tin alloy fine and stable. Further, when the content of Zr is more than 0.25 mass%, coarse intermetallic compounds are likely to be formed, and the surface appearance after the acid-resistant treatment is likely to cause color spots. Therefore, the content of 'Zr' is 0.25 mass% or less. (Si: 0.7% by mass or less, Fe: 0.8% by mass or less, Μη: 〇.8 mass% or less, Cu: 0.5% by mass or less, and Ti: 0.1% by mass or less)

Si、Fe、Mn、Cr、Ti之各效果，由於與Al-Mg系合金 者相同，故予以省略。 而且’於Al-Mg系合金、Al-Mn系合金、Al-Mg-Si系合 -20- 1355301 熔體化處理及時效處理實施調質處理。：而且，此等處理亦 可平滑化處理步驟S70後進行。而且，例如日本特開昭63-115617公報中揭示’可藉由實施熱處理，提高表面之平坦 度。 (平滑化處理步驟） 平滑化處理步驟S70，係爲使鋁合金熱延板之表面（ φ 壓延面）予以平滑化，並調整板厚的步驟。 此處，熱延板之表面的除去厚度，每一面爲2〜5mm 。藉由使除去厚度爲2mm以上時，使平坦度 '板厚之不均 性適當地調整，且可抑制因瑕疵之表面缺陷。 而且，如上所述，近年來不受原板沒有缺陷所拘束， 實施耐酸鋁處理或電鏟處理等之表面處理後，朝壓延平行 方向產生約3μπι長度之黑色線條狀表面缺陷的缺點，惟本 發明人等再三深入硏究該原因的結果，發現防止鑄塊破裂 • 或鑄造時之鑄塊微細化劑（結晶粒微細化劑）之Ti-B，係 爲漿料造塊之鑄型附近之急冷凝固部溶解、所殘留者。因 此，使除去厚度爲2mm以上，即使有鑄塊微細化劑之Ti-B 之溶解、殘留，亦可除去該物，故即使進行耐酸鋁處理或 電鍍處理，也不會有產生黑色線條狀表面缺陷的情形。而 且，就處理性或成本而言，除去厚度爲5mm以下。 平滑化處理方法，可使用端銑刀（end mill )切削或 鑽石刀（diamond bite )切削等之切削法、使表面以砥石 等切削的硏削法、拋光（buffing )硏磨等之硏磨法等，惟 -25- 1355301 不受此等所限制。 此外，於平滑化處理步驟S70中，藉由平坦度、板厚 之不均勻性、瑕疵或黑色線條等，抑制表面缺陷後，再實 施髮線加工（hair line process )。藉由實施髮線加工處理 ’可對厚板表面施加壓延目。髮線加工的方法，帶式、或 滾輪式等之硏磨方法，係爲已知，可採用任一方法，亦可 帶式、或滾輪式等之髮線加工處理時所使用的硏磨不織布 ’例如由作爲砥粒種之氧化鋁、碳化矽、二氧化鉻等之單 體、或此等之混合物’與樹脂或骨膠等之黏著劑所形成， 係爲已知’砥粒編號例如市售品之較粗的# 1 2 〇〜# 2 2 0 »而The respective effects of Si, Fe, Mn, Cr, and Ti are the same as those of the Al-Mg-based alloy, and therefore will be omitted. Further, the tempering treatment was carried out in an Al-Mg-based alloy, an Al-Mn-based alloy, an Al-Mg-Si-based -20-1355301 melt treatment and a aging treatment. : Moreover, these processes can also be performed after the smoothing process S70. Further, for example, it is disclosed in Japanese Laid-Open Patent Publication No. SHO63-115617 that the flatness of the surface can be improved by performing heat treatment. (Smoothing Process Step) The smoothing process step S70 is a step of smoothing the surface (φ rolling surface) of the aluminum alloy heat-expanding plate and adjusting the thickness of the plate. Here, the thickness of the surface of the heat-expanding plate is 2 to 5 mm on each side. When the thickness is 2 mm or more, the unevenness of the flatness 'thickness is appropriately adjusted, and surface defects due to flaws can be suppressed. Further, as described above, in recent years, the original sheet is not restricted by the defect, and after the surface treatment such as the alumite treatment or the shovel treatment, the black line-like surface defect having a length of about 3 μm is generated in the parallel direction of the rolling, but the present invention After repeated investigations into the cause of this cause, it was found that Ti-B, which prevents cracking of the ingot, or the ingot of the ingot in the casting (crystal grain refiner), is quenched near the mold of the slurry agglomerate. The solidified part is dissolved and remains. Therefore, if the thickness is 2 mm or more, even if the Ti-B of the ingot refining agent is dissolved or left, the object can be removed. Therefore, even if an alumite treatment or a plating treatment is performed, a black line-like surface is not generated. The situation of the defect. Further, in terms of handleability or cost, the thickness is removed to 5 mm or less. The smoothing method can be performed by a cutting method such as an end mill cutting or a diamond bite cutting, a boring method in which a surface is cut by vermiculite, or a honing method such as buffing honing. Etc. However, -25-1355301 is not subject to these restrictions. Further, in the smoothing step S70, the surface defects are suppressed by flatness, unevenness of the thickness, flaws, or black lines, and then the hair line process is performed. The rolling target can be applied to the surface of the slab by performing the hairline processing. The method of hairline processing, the belt type, or the roller type, etc. are known, and any method can be used, and the honing non-woven fabric used in the hairline processing such as belt type or roller type can be used. 'For example, it is formed from an adhesive of alumina, tantalum carbide, chromium dioxide or the like as a cerium seed, or a mixture thereof, and an adhesive such as a resin or a bone cement, and is known as a 'grain number, for example, commercially available. The thicker #1 2 〇~# 2 2 0 »

I 且’使用帶式或滾輪式回轉外徑爲φ 400mm之硏磨不織布 時’由於含有防止烘烤的油，故以1500 rpm以下之回轉數 進行髮線加工處理較佳，惟不受此等之條件所限制。 而且，有關因瑕疵之表面缺陷問題，可以人的肉眼所 辨識的瑕疵大小，深度爲8 μπι以上，於檢査時無法判斷的 瑕疵大小爲20μιη爲止，8〜20μπι深度藉由異物或輥瑕疵產 生押入’該缺陷不爲原有的功能的缺陷。因此，由於該押 入瑕疵可藉由實施髮線加工處理（加工代工約2〜3μιη)， 使厚板表面之平滑部與瑕疵之境界形成平滑的狀態，故具 有可容易判斷功能性缺陷之效果。此外，無視經濟性時， 即使僅進行髮線加工處理，只要是每一面切削2mm以上時 ，可得本發明之效果。 其次，該經製造的鋁合金厚板，再藉由檢查步驟S80 ，檢查有關變形、板厚、及表面瑕疵等後，藉由樹脂薄膜 -26- 1355301 被覆步驟S 90，使表裏面以樹脂薄膜予以被覆。 【實施方式】 於上述中，說明有關爲實施本發明之最佳形態，於下 述中，確認本發明效果之實施例與不滿足本發明要件之比 較例相比時’具體地說明。而且，本發明不受該實施例所 限制。 [實施例1 :供試材料製作] (Al-Mg系合金） 使表1所示之合金No.5a〜5v之組成的鋁合金（5k: JIS5052合金、51 : JIS5083合金、5v沒有添加Ti、B)溶解 ，且進行脫氫處理、過濾後，予以鑄造，製作板厚500mm 之鑄塊。使該鑄塊在5 00 °C下進行加熱4小時，予以均熱處 理後，進行熱間壓延處理，製作厚度約25mm、與厚度約 20 mm之鋁合金熱延板。使該鋁合金熱延板切成壓延方向 長度2000mmx寬度1 000mm後，對壓延面（兩面）而言進行 平滑化處理，形成厚度2 0 mm之鋁合金厚板（切斷板）。 而且，有關含有Ti者，爲防止鑄塊破裂情形時，添加Ti-B 母合金。平滑化處理係以端銑刀加工、端銑刀加工+髮線 加工（藉由帶式硏磨不織布）、髮線加工等3種方法比較 其效果。此外，實施端銑刀加工處理者，係使用厚度約爲 2 5 mm之鋁合金熱延板，且僅實施髮線加工處理者，係使 用厚度約20m之鋁合金熱延板。 -27- 1355301 端銑刀加工處理，係改造WASSER GmbH (德國之機 械製造商、GmbH爲股份有限公司）之端銑刀加工機（鉄 刀）使用。粗片係超硬，加工片係爲鑽石，加工代工係爲 就零點而言之圓盤的押入量，總値約爲2.5 mm/單片下予以 調整進行加工。 具體而言，圓盤下面之圓周附近裝設有30個粗片、2 個加工片，使圓盤降落於被加工物後，予以回轉，藉由送 至板長度方向進行切削加工處理。而且，由於加工處理片 之飛出量較粗片稍微飛出下予以裝設，使粗片之切削面切 削成繼後的加工處理片後，繼續切削的形態》 髮線加工處理，係使野水機械股份有限公司（Nomizu Machine Mfg. Co.，Ltd)製之鋁板拋光硏磨機器在拋光硏 磨輥部上可裝設硏磨不織布滾輪予以改造、使用。滾輪係 使用光陽社股份有限公司（KOYO-SHA Co.，Ltd)製之聚 乳膠（POLITEX;註冊商標）KF滾輪 ΜΑ (粗目（#150) 、外徑φ 400mm、油含浸，砥粒種使用褐色熔融氧化鋁、 黏合劑使用樹脂黏合劑）》 然後，以加工代工約爲3. Ομπι/單片所形成的條件（振 盪（2次來回））實施硏磨處理。而且，硏磨代工係使試 驗的硏磨部之段差以Vecoo instruments Inc •製（美國） 之「WYKO NT3 3 00 (表面形狀測定系統）」測定形狀， 測定凹凸之深度，予以計測確認。 (A卜Μη系合金） -28- 1355301 使表1所示之合金No.3a〜3e之組成的鋁合金（3e:沒 有添加Ti、B)溶解，且進行脫氫處理、過濾後，予以鑄 造，製作板厚5 00mm之鑄塊》使該鑄塊進行熱間壓延處理 ，製作厚度約25mm、與厚度約20mm之鋁合金熱延板。使 該鋁合金熱延板切成壓延方向長度2000mmx寬度1 000mm後 ，對壓延面（兩面）而言進行平滑化處理，形成厚度 2 0mm之鋁合金厚板（切斷板）。而且，有關含有Ti者，爲 防止鑄塊破裂情形時，添加Ti-B母合金。平滑化處理係以 端銑刀加工、端銑刀加工+髮線加工（藉由帶式硏磨不織 布）、髮線加工等3種方法比較其效果。而且，實施端銑 刀加工處理者，係使用厚度約爲25mm之鋁合金熱延板’ 且僅實施髮線加工處理者，係使用厚度約20m之鋁合金熱 延板。此外’有關端銑刀加工、髮線加工之方法’係與前 述Al-Mg系合金時相同。I and 'When using a belt or roller type honing non-woven fabric with an outer diameter of φ 400 mm, 'Because it contains oil for preventing baking, it is better to perform the wire processing at a number of revolutions of 1500 rpm or less, but it is not necessary. The conditions are limited. Moreover, regarding the surface defect caused by the flaw, the size of the crucible which can be recognized by the human eye is 8 μπι or more, and the size of the crucible which cannot be judged at the time of inspection is 20 μm, and the depth of 8 to 20 μm is generated by foreign matter or roller crucible. 'This defect is not a defect of the original function. Therefore, since the entanglement can be performed by performing the hairline processing (processing: about 2 to 3 μm), the smooth portion of the surface of the slab and the boundary of the slab are formed in a smooth state, so that the effect of the functional defect can be easily judged. . Further, in the case of ignoring the economy, even if only the hairline processing is performed, the effect of the present invention can be obtained as long as the surface is cut by 2 mm or more. Next, the manufactured aluminum alloy thick plate is further covered with a resin film by a resin film -26-1355301, and a resin film is formed by a resin film -26-1355301 after inspecting the deformation, the thickness, and the surface flaw by the inspection step S80. Be covered. [Embodiment] In the above, the best mode for carrying out the invention will be described. In the following, an embodiment in which the effects of the present invention is confirmed will be described in detail when compared with a comparative example that does not satisfy the requirements of the present invention. Moreover, the invention is not limited by the embodiment. [Example 1 : Preparation of test material] (Al-Mg-based alloy) Aluminum alloy having the composition of alloy Nos. 5a to 5v shown in Table 1 (5k: JIS5052 alloy, 51: JIS5083 alloy, 5v without Ti added, B) Dissolved, dehydrogenated, filtered, and cast to produce an ingot having a thickness of 500 mm. The ingot was heated at 500 ° C for 4 hours, subjected to soaking treatment, and then subjected to hot rolling treatment to prepare an aluminum alloy heat-expanding plate having a thickness of about 25 mm and a thickness of about 20 mm. After the hot-rolled aluminum alloy sheet was cut into a rolling direction and the length was 2000 mmx and the width was 1 000 mm, the rolled surface (both sides) was smoothed to form an aluminum alloy thick plate (cutting plate) having a thickness of 20 mm. Further, in the case of containing Ti, in order to prevent the ingot from being broken, a Ti-B mother alloy is added. The smoothing process compares the effects of end mill machining, end mill machining + hairline machining (by belt honing non-woven fabric) and hairline machining. In addition, the end mill processing processor is made of an aluminum alloy heat-expanding plate having a thickness of about 25 mm, and only a hairline processing processor is used, and an aluminum alloy heat-expanding plate having a thickness of about 20 m is used. -27- 1355301 The end mill is processed and used to transform the end mill cutter (knife) of WASSER GmbH (German machine manufacturer, GmbH). The thick film is super hard, the processed piece is made of diamond, and the processing foundry is the amount of the disk in the zero point, and the total 値 is about 2.5 mm/one piece is adjusted for processing. Specifically, 30 thick pieces and two processed pieces are placed near the circumference of the lower surface of the disk, and the disk is dropped on the workpiece, and then rotated, and processed by cutting to the longitudinal direction of the plate. In addition, since the amount of flying out of the processed sheet is slightly larger than that of the thick sheet, the cutting surface of the thick sheet is cut into the subsequent processed sheet, and the cutting form is continued. The aluminum plate polishing and honing machine manufactured by Nomizu Machine Mfg. Co., Ltd. can be modified and used by honing non-woven fabric rollers on the polishing honing roller. The roller system is a polylactic acid (POLITEX; registered trademark) KF roller 制 manufactured by KOYO-SHA Co., Ltd. (thickness (#150), outer diameter φ 400 mm, oil impregnation, and glutinous grains are melted in brown. Alumina and a binder are used as a resin binder.) Then, a honing treatment is carried out under the conditions (oscillation (2 times back and forth)) of a processing of about 3. Ομπι/monolith. In addition, the honing foundry system measures the shape of the honing section of the test by the "WYKO NT3 3 00 (surface shape measuring system)" manufactured by Vecoo Instruments Inc. (USA), and measures the depth of the unevenness and measures it. (A Μ 系-based alloy) -28- 1355301 The aluminum alloy (3e: no Ti or B added) having the composition of Alloy Nos. 3a to 3e shown in Table 1 was dissolved, dehydrogenated, filtered, and then cast. An ingot having a thickness of 500 mm was produced. The ingot was subjected to hot rolling treatment to prepare an aluminum alloy heat-expanding plate having a thickness of about 25 mm and a thickness of about 20 mm. After the hot-rolled aluminum alloy sheet was cut into a rolling direction length of 2000 mm x a width of 1 000 mm, the rolled surface (both sides) was smoothed to form an aluminum alloy thick plate (cutting plate) having a thickness of 20 mm. Further, in the case of containing Ti, a Ti-B mother alloy is added in order to prevent the ingot from being broken. The smoothing process compares the effects of end mill machining, end mill machining + hairline machining (by belt honing and weaving), and hairline machining. Further, the end mill cutter processor is an aluminum alloy heat spreader plate having a thickness of about 25 mm and is only subjected to a hairline processing, and an aluminum alloy heat spreader having a thickness of about 20 m is used. Further, the method of processing the end mill and the processing of the hairline is the same as that of the above-described Al-Mg alloy.

-29- 1355301 【表1】 合金 鋁合金成分誠(質量％) No. Mg Si Fe Cu Mn Cr Zn Ti Al** 5a 2.6 0.1 0.4 - - - - 0.01 殘留成分 5b Z6 0·1 0.4 - 0.3 - - 0.01 殘留成分 5c 4.4 0.1 0.4 1 - - - - 0.01 殘留成分 5d 7.0 0.1 0.4 - - - - 0.01 殘留成分 5e 10.5 0.1 0.4 - - - - 0.01 殘留成分 5f 4.4 0.3 0.5 0.3 - - - 0.01 殘留成分 5g 4.4 0.1 0.3 - 0.05 - - 0.01 殘留成分 5h 4.4 0.1 0.3 — - 0.05 - 0.01 殘留成分 5i 4.4 0.1 0.3 - 0.7 0.3 - 0.01 殘留成分 5j 4.4 0.1 0.3 - 0.05 - 0.3 0.01 殘留成分 5k 2.5 0.1 0.3 - - 0.15 - 0.01 殘留成分 51 4.4 0.1 0.2 - 0.6 - - 0.01 殘留成分 5m* 1.4* 0.1 0.4 - 产 - 0.01 殘留成分 5n * 13.0* 0.1 0.4 - - - - 0.01 殘留成分 5o * 4.4 0.8* 0.4 - - - - 0.01 殘留成分 5d * 4.4 0.1 1.0* - - — - 0.01 殘留成分 5q * 4.4 0.1 0.4 0.7* - - - 0.01 殘留成分 5r* 4.4 0.1 0.4 - 1.1 * - - 0.01 殘留成分 5s * 4.4 0.1 0.4 - - 0.6* - 0.01 殘留成分 5t * 4.4 0.1 0.4 - - - 0.5* 0.01 殘留成分 5u * 4.4 0.1 0.4 - - - - 0_1护 殘留成分 5v 2.6 0.1 0.4 - - - - — 殘留成分 3a - 0.1 0.3 - 0.5 - - 0.01 殘留成分 3b - 0.1 0.4 - 0.9 - - 0.01 殘留成分 3c * - 0.1 0.4 - 0.2* — - 0.01 殘留成分 3d * - 0.1 0.3 - 1.7* - - 0.01 殘留成分 3e - 0.1 0.3 - 0.5 - - — 殘留成分 *:適當範圍外 :含有不可避免的雜質-29- 1355301 [Table 1] Alloy aluminum alloy composition (% by mass) No. Mg Si Fe Cu Mn Cr Zn Ti Al** 5a 2.6 0.1 0.4 - - - - 0.01 Residual component 5b Z6 0·1 0.4 - 0.3 - - 0.01 Residual component 5c 4.4 0.1 0.4 1 - - - - 0.01 Residual component 5d 7.0 0.1 0.4 - - - - 0.01 Residual component 5e 10.5 0.1 0.4 - - - - 0.01 Residual component 5f 4.4 0.3 0.5 0.3 - - - 0.01 Residual component 5g 4.4 0.1 0.3 - 0.05 - - 0.01 Residual component 5h 4.4 0.1 0.3 — - 0.05 - 0.01 Residual component 5i 4.4 0.1 0.3 - 0.7 0.3 - 0.01 Residual component 5j 4.4 0.1 0.3 - 0.05 - 0.3 0.01 Residual component 5k 2.5 0.1 0.3 - - 0.15 - 0.01 Residual component 51 4.4 0.1 0.2 - 0.6 - - 0.01 Residual component 5m* 1.4* 0.1 0.4 - Yield - 0.01 Residual component 5n * 13.0* 0.1 0.4 - - - - 0.01 Residual component 5o * 4.4 0.8* 0.4 - - - - 0.01 Residual component 5d * 4.4 0.1 1.0* - - - - 0.01 Residual component 5q * 4.4 0.1 0.4 0.7* - - - 0.01 Residual component 5r* 4.4 0.1 0.4 - 1.1 * - - 0.01 Residual component 5s * 4.4 0.1 0.4 - - 0.6 * - 0.01 Residual component 5t * 4.4 0.1 0.4 - - - 0.5* 0.01 Residual component 5u * 4.4 0.1 0.4 - - - - 0_1 Residual component 5v 2.6 0.1 0.4 - - - - - Residual component 3a - 0.1 0.3 - 0.5 - - 0.01 Residual component 3b - 0.1 0.4 - 0.9 - - 0.01 Residual component 3c * - 0.1 0.4 - 0.2* — - 0.01 Residual component 3d * - 0.1 0.3 - 1.7* - - 0.01 Residual component 3e - 0.1 0.3 - 0.5 - - - Residual component *: Appropriate range: Contains unavoidable impurities

[實施例1 :評估] 鲁 以所得的鋁合金厚板進行下述之評估，結果如表2,3 所示。而且，亦製作沒有實施平滑化處理的鋁合金熱延板 (厚度爲20mm )，作爲比較例予以評估。此外，合金 No. 5η係如下所述，由於無法製作鋁合金熱延板，故無法 實施下述之處理及評估，表2,3係以「-」表示。 (平坦性） 平坦性評估，係測定每1 m之供試材料之壓延方向的翹 -30- 1355301 曲量（平坦度）。平坦性之合格基準，係平坦度爲0.2 mm/m以下。 (板厚精度） 自供應材料之4角、及壓延方向之邊長度的一半部分 朝寬度方向之內側20mm的部位，合計6處之板厚，使用微 測定器進行測定。全部6處之板厚皆爲20.0±0.06mm ( 19.94〜20.06mm)之範圍者，板厚精度優異，評估爲「◎ 」，20.0 土 0.10mm(20.0mm±0.5o/〇、 19.90 〜20.10mm)之 範圍者爲佳，評估爲「〇」。 (強度） 自供試材料藉由JIS5號切出拉伸試驗片。以該試驗片 藉由JIS Z2241實施拉伸試驗處理，測定拉伸強度及耐力（ 0.2 %耐力）。強度之合計基準，合金No.5a〜5u(Al〜Mg 系合金）之拉伸強度爲18 ON/mm2以上，合金No.3a〜3d ( A1〜Μη系合金）之拉伸強度爲9 0N/mm2以上。 (表面性質） 爲評估藉由平滑化處理對表面性質之影響，在供試材 料（各40張）實施耐酸鋁處理，觀察其表面之外觀。 在供試材料之表面上以硫酸耐酸鋁處理（1 5 %硫酸、 2〇°C、電流密度2A/dm2 )形成厚度ΙΟμπι之耐酸鋁皮膜。然 後，觀察因表面瑕疵之表面性質及因黑色線條之表面性質 -31 - 1355301 &lt;尉酸鋁處理後因瑕疵之表面性質評估&gt; 觀察該經耐酸鋁處理的表面之外觀，40張以肉眼判斷 的切斷板中以因瑕疵之表面性質評估沒有1張時、極佳爲 ^ ◎」，40張以肉眼判斷的切斷板中以因瑕疵之表面性質 評估時有1〜4張、佳爲「〇」，40張以肉眼判斷的切斷板 中以因瑕疵之表面性質評估有5張以上時、不佳爲「Xj 。 &lt;耐酸鋁處理後因黑色線條之表面性質評估&gt; 觀察該經耐酸鋁處理的表面之黑色線條（沒有功能缺 陷），以肉眼觀察沒有黑色線條者、藉由黑色線條評估表 面性質爲佳者「◎」，以肉眼觀察有黑色線條者、藉由黑 色線條評估表面性質爲不佳者「X」。 另外，調查有關因表面之色斑的表面性質。而且，該 表面性質由於在本發明中全部企求的表面性質沒有超過， 即使沒有滿足該表面性質時，滿足因瑕疵及黑色線條之表 面性質者，有關表面性質，係爲達成本發明之最低限的目 的。 &lt;因耐鋁酸處理後之色斑之表面性質評估&gt; 觀察前述經耐酸鋁處理的表面之外觀，外觀沒有色斑 者以因色斑之表面性質評估佳、爲「〇」，有色斑者以因 色斑之表面性質評估不佳、爲。 -32- 1355301 而且，端銑刀加工+髮線加工、及僅髮線加工之強度 値，由於與僅端銑刀加工之強度的値相同，故表中省略記 載。[Example 1: Evaluation] Lu The following evaluation was carried out on the obtained aluminum alloy thick plate, and the results are shown in Tables 2 and 3. Further, an aluminum alloy heat-expanding plate (thickness: 20 mm) which was not subjected to the smoothing treatment was also produced, and was evaluated as a comparative example. Further, the alloy No. 5η is as follows. Since the aluminum alloy heat-expanding plate cannot be produced, the following treatment and evaluation cannot be performed, and Tables 2 and 3 are indicated by "-". (Flatness) The flatness evaluation is performed by measuring the curl amount (flatness) of -30 - 1355301 in the rolling direction of the test material per 1 m. The flatness is based on a flatness of 0.2 mm/m or less. (Shear thickness accuracy) The thickness of the four corners from the four corners of the supply material and the length of the side in the rolling direction was 20 mm in the width direction, and the thickness was measured at six places, and the measurement was performed using a micrometer. The thickness of all 6 places is 20.0±0.06mm (19.94~20.06mm), and the plate thickness is excellent. The evaluation is “◎”, 20.0 soil 0.10mm (20.0mm±0.5o/〇, 19.90~20.10mm) The scope of the survey is better, and the assessment is "〇". (Strength) A tensile test piece was cut out from the test material by JIS No. 5. The test piece was subjected to a tensile test treatment by JIS Z2241, and tensile strength and endurance (0.2% proof) were measured. The total strength is based on the tensile strength of alloy No. 5a to 5u (Al to Mg alloy) of 18 ON/mm2 or more, and the tensile strength of alloy No. 3a to 3d (A1 to Μ-type alloy) is 90 N/ Mm2 or more. (Surface properties) In order to evaluate the influence on the surface properties by the smoothing treatment, the test materials (40 sheets each) were subjected to an alumite treatment, and the appearance of the surface was observed. An alumite film having a thickness of ΙΟμπι was formed on the surface of the test material by an alumite treatment of sulfuric acid (15% sulfuric acid, 2 ° C, current density 2 A/dm 2 ). Then, observe the surface properties of the surface flaw and the surface properties due to the black line -31 - 1355301 &lt;Evaluation of the surface properties of the tantalum after treatment with aluminum niobate&gt; Observe the appearance of the alumite-treated surface, 40 eyes to the naked eye In the judged cut sheet, when there is no one sheet due to the surface property evaluation of the crucible, it is excellent as ^ ◎", and 40 sheets of the cut sheet judged by the naked eye have 1 to 4 sheets evaluated because of the surface properties of the crucible. For "〇", 40 pieces of the cut plate judged by the naked eye are evaluated as "Xj when the surface properties of the enamel are evaluated." <jj. &lt;Evaluation of surface properties of black lines after acid-resistant aluminum treatment> The black line of the alumite-treated surface (with no functional defects), the naked eye is observed by the naked eye, the surface property is evaluated by the black line, and the black line is observed by the naked eye. Evaluate the surface properties as "X". In addition, investigate the surface properties of the spots due to the surface. Moreover, the surface property is not exceeded by all the surface properties sought in the present invention, and even if the surface properties of the black and white lines are satisfied, the surface properties are satisfied to achieve the minimum of the present invention. purpose. &lt;Evaluation of surface properties of stains after resistance to aluminic acid treatment&gt; Observing the appearance of the surface treated with the alumite treatment, the appearance of the stains is not evaluated, and the surface properties of the stains are evaluated as "〇", colored Plaques are poorly evaluated due to the surface properties of the stains. -32- 1355301 Moreover, the strength of the end mill machining + hairline processing and the hairline only processing is the same as the strength of the end mill machining only, so the table is omitted.

表2】 鉬合 藉由端统刀加工平滑化處理 藉由端誅刀加工+髮線加工^平滑化處理 No. 平酿 (mm/m) 強度(N/mm1) 耐麟腿後 平酿 腿 精度 拉伸酿 耐力 挪疵之 表面 因黒酿條 之表面賊 因色斑之 表面賊 (mm/m) 精度 因瑕班之 表瓸性質 因黑色線怿 之表面性質 因颂之 表面韻 5a 0.15 ◎ 217 102 ◎ 〇 〇 0.14 ◎ ◎ 〇 〇 5b 0.15 © 228 110 ◎ 〇 〇 0.15 ◎ ◎ 0 〇 5c 0.16 ◎ 294 143 ◎ 〇 〇 0.16 ◎ ◎ 〇 〇 5d 0.t8 ◎ ' 331 170 @ 〇 〇 0.17 @ @ 0 0 5e 0.19 385 186 ◎ 〇 〇 0.18 ◎ ◎ 〇 〇 5f 0.18 ◎ 309 139 ◎ 〇 〇 0.18 ◎ 〇 〇 5e 0.16 ◎ 305 146 ◎ 〇 〇 0.16 ◎ 〇 〇 &lt;5h 0.16 314 145 ◎ 〇 〇 0.15 ◎ ◎ 〇 〇 5\ 0.17 318 155 ◎ 〇 〇 0.17 ◎ ◎ 〇 〇 5j 0.18 ◎ 305 144 ◎ 〇 〇 0.18 ◎ 〇 〇 5k 0.16 222 108 ◎ 〇 〇 0.15 @ ◎ 0 〇 51 0.18 307 145 ◎ 〇 〇 0.18 ◎ ◎ 〇 〇 5m* 0.15 ◎ 171 69 ◎ 〇 〇 0.15 ◎ ◎ 〇 〇 5n * — — — - - — — — — — 一 5o* 0.17 &lt;§&gt; 322 160 @ 〇 X 0.17 ◎ ◎ 0 X 5d * 0.17 ◎ 306 150 ◎ 〇 X 0.16 ◎ ◎ 〇 X 5q * 0.18 ◎ 320 163 ◎ 〇 〇 0.18 ◎ ◎ 0 〇 5r* 0.17 ◎ 324 162 ◎ 〇 X 0.17 ◎ ◎ 〇 X 5s * 0.18 ◎ 322 158 〇 X 0,17 © 0 % St* 0.17 ◎ 305 146 ◎ 〇 〇 0.1? ◎ ◎ 〇 〇 5u * 0.18 310 147 ◎ 〇 〇 0.18 @ 0 〇 5v 0.15 ◎ 215 101 ◎ 〇 〇 0.14 ◎ ◎ 〇 〇 3« CU5 © 94 38 @ 〇 〇 0.15 ◎ 〇 〇 3b 0.16 ◎ 103 41 @ 〇 〇 0.15 ◎ 0 〇 3c聿 0.16 ◎ 84 37 〇 〇 0.1 Θ ◎ ◎ 〇 〇 3d* 0.17 ◎ 117 49 ◎ 〇 X 0.16 © 0 X 3e 0.15 ◎ 92 37 ◎ 〇 〇 0.14 ◎ ◎ 〇 〇 適當範圍外 -33- 1355301Table 2] Molybdenum is smoothed by end knife processing by end boring processing + hairline processing ^ smoothing treatment No. Flat (mm/m) strength (N/mm1) Accurately stretched the endurance of the surface of the endurance due to the surface of the thief due to the surface of the thief (mm / m) Accuracy due to the nature of the class 因 因 因 因 因 因 因 因 因 因 因 因 5 5 5 5 5 5 5 5 5 5 5 5 217 102 ◎ 〇〇 0.14 ◎ ◎ 〇〇 5b 0.15 © 228 110 ◎ 〇〇 0.15 ◎ ◎ 0 〇 5c 0.16 ◎ 294 143 ◎ 〇〇 0.16 ◎ ◎ 〇〇 5d 0.t8 ◎ ' 331 170 @ 〇〇 0.17 @ @ 0 0 5e 0.19 385 186 ◎ 〇〇 0.18 ◎ ◎ 〇〇 5f 0.18 ◎ 309 139 ◎ 〇〇 0.18 ◎ 〇〇 5e 0.16 ◎ 305 146 ◎ 〇〇 0.16 ◎ 〇〇 &lt; 5h 0.16 314 145 ◎ 〇〇 0.15 ◎ ◎ 〇〇5\ 0.17 318 155 ◎ 〇〇 0.17 ◎ ◎ 〇〇 5j 0.18 ◎ 305 144 ◎ 〇〇 0.18 ◎ 〇〇 5k 0.16 222 108 ◎ 〇〇 0.15 @ ◎ 0 〇 51 0.18 307 145 ◎ 〇〇 0.18 ◎ ◎ 〇 〇5m* 0.15 ◎ 171 69 ◎ 〇〇 0 .15 ◎ ◎ 〇〇5n * — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — — X 5q * 0.18 ◎ 320 163 ◎ 〇〇 0.18 ◎ ◎ 0 〇 5r* 0.17 ◎ 324 162 ◎ 〇X 0.17 ◎ ◎ 〇X 5s * 0.18 ◎ 322 158 〇X 0,17 © 0 % St* 0.17 ◎ 305 146 ◎ 〇〇 0.1? ◎ ◎ 〇〇 5u * 0.18 310 147 ◎ 〇〇 0.18 @ 0 〇 5v 0.15 ◎ 215 101 ◎ 〇〇 0.14 ◎ ◎ 〇〇 3 « CU5 © 94 38 @ 〇〇 0.15 ◎ 〇〇 3b 0.16 ◎ 103 41 @ 〇〇0.15 ◎ 0 〇3c聿0.16 ◎ 84 37 〇〇0.1 Θ ◎ ◎ 〇〇3d* 0.17 ◎ 117 49 ◎ 〇X 0.16 © 0 X 3e 0.15 ◎ 92 37 ◎ 〇〇0.14 ◎ ◎ 〇〇 Appropriate range外-33- 1355301

Is】 耐酸鋁處理後 mm 0 0 0 o 0 o o O 0 0 o o o 1 X X o X X O 〇 o o 0 0 X 〇 進酞 _ X X X X X X X X X X X X X 1 X X X X X X X o X X X X 〇 鋁合金熱延板 因瑕庇之 表面性質 X X X X X X X X X X X X X 1 X X X X X X X X X X X X X 強度(N/mm2) 耐力 S CO Ο CO CQ S in σ&gt; CM in 穿 这 Csi CM Ln CNJ O) 1 CO co S CNJ in 字 •^· s m in 00 in s u&gt; ir&gt; 拉伸強度 CM CVJ CM CM esj σ&gt; C4 o 00 &lt;0 CO 00 σ&gt; CVJ a&gt; CM CO &lt;y&gt; cvi g CO CM O) o w Lft 卜 1 CM σ&gt; CM 0 01 CvJ 00 Oi CM CM 另 09 CO CM co a&gt; CM ¢0 00 ¢0 O) 0 CM »· Η 精度 ◎ ◎ 0 o 0 ◎ o o 0 o ◎ o ◎ 1 ◎ o 〇 ◎ o 〇 〇 ◎ ◎ 0 ◎ 0 ◎ 卒坦度 (mm/m) 〇 0.42 | 0.50 | 1 0.62 1 0.69 I 1 047 j 0.48 1 Q-47 | 0.50 0.48 0.43 0.49 1 0.42 1 0.48 1 0.50 1 0.49 1 0.48 1 0.48 1 1 0.50 1 0.50 1 0.40 〇 1 0.42 〇 1 0.44 0 鋁合金厚板 藉由髮線加工之平滑化處理 耐酸鋁處理後 因色斑之 表面性質 0 O 0 O 0 〇 0 o o O O 〇 O 1 X X 〇 X X O O O 〇 〇 〇 X 0 骧却 mM 咖 X X X X X X X X X X X X X ] X X X X X X X 0 X X X X 0 因瑕疵之 表面性質 0 〇 o o 0 o 0 o 〇 0 o 〇 o 1 〇 〇 o 〇 〇 〇 〇 0 〇 〇 0 0 0 1 a 精度 ◎ ◎ 0 o 0 ◎ 0 o 〇 0 ◎ 〇 ◎ 1 ◎ 0 o ◎ o o o ◎ ◎ 0 ◎ 0 ◎ Μ (mm/m) 〇 O 0.50 I to o 0.68 1 0.47 | 0.48 | i 0-47 | i 0.49 1 0.46 0.43 0.48 1 0-42 1 1 1 0.48 1 0.50 1 0.48 ! 1 0.48 1 0.47 1 0.50 1 0.49 1 0.40 〇 5 0 0 1 0.43 0 合金 6 ¢0 m 5 in 5 ίο in io in 55 1 5m*| 1 5n * 5o * in 箐 5r ♦ 5s * 箐 \Ά 1 5u * l〇 «〇 CO &lt;0 1 3c * 3d* Φ CO 欢囫留麵頸* -34- 1355301 由合金No. 5a〜51、及5v所形成的鋁合金厚板，添加 元素之含量爲適當的範圍內，由於在表面上實施適當的平 滑化處理，強度、平坦性、板厚精度、及表面性質佳。而 且，與沒有實施平滑化的鋁合金熱延板相比時，可得充分 的強度及良好的表面性質。對此而言，由合金No. 5m所形 成的鋁合金厚板，由於Mg含量不足，無法得到充分的強度 。另外，由合金Νο·5η所形成的鋁合金厚板，由於Mg含量 過剩時，會產生鑄造破裂情形，無法製作供試材料。由合 金No.5o、5p、5r、5s所形成的鋁合金厚板，由於Si、Fe、 Μη、Cr之各含量過剩，會形成粗大的金屬間化合物，在耐 酸鋁處理後之表面外觀上會產生色斑。由合金No.5q、5t 、5u所形成的鋁合金厚板，Cu、Zn、Ti之含量各大於適當 的範圍，與此等之元素在適當範圍內之合金No.5f、5j、5c 相比時，沒有提高強度及表面性質之效果。 此外，有關表面平滑化處理之方法不同處，與除去量 少之僅髮線加工相比時，除去量適當的端銑刀加工+髮線 加工、或僅端銑刀加工時，可確認提高因瑕疵之表面性質 。而且，在習知的熱延板之切斷板上有瑕疵，包含以肉眼 觀察可見的尺寸之功能完全沒有問題的微小瑕疵所判斷者 ’僅實施髮線加工之切斷板上所見的瑕疵，可以目視明顯 判斷的瑕疵。因此，僅髮線加工，亦可確認容易區別功能 缺陷的效果。 另外，僅髮線加工時，由於除去量少時，無法防止產 生黑色線條，僅端銑刀加工、或端銑刀加工+髮線加工時 -35- 1355301 ，由於除去量適當，確認可防止黑色線條產生。而且， 5 v所形成的鋁合金厚板，於漿料造塊時沒有使用鑄塊微 化劑之Ti-B時：沒有受到表面平滑化處理之方法的不同 所影響，確認表面平滑化處理之方法皆可防止黒色線條 生° 由合金No.3a、3b、3e所形成的鋁合金厚板，添加 素之含量爲適當的範圍內，由於在表面上實施適當的平 化處理，強度、平坦性、板厚精度、及表面性質良好。 且，與沒有實施平滑化處理的鋁合金熱延板相比時，可 充分的強度及良好的表面性質。對此而言，由合金No 所形成的鋁合金厚板，由於Μη之含量不足，無法得到充 的強度。另外，由合金No .3d所形成的鋁合金厚板，由 Μη之含量過剩，會形成粗大的金屬間化合物，在耐酸鋁 理後之表面外觀上產生色斑。 而且，有關表面平滑化處理之方法的不同處，與僅 施除去量少的髮線加工相比時，除去量適當的端銑刀加 +髮線加工、或僅實施端銑刀加工時，可確認提高因瑕 之表面性質。而且，在習知的熱延板之切斷板上有瑕疵 包含以肉眼觀察可見的尺寸之功能完全沒有問題的微小 疵所判斷者，僅實施髮線加工之切斷板上所見的瑕疵， 以目視明顯判斷的瑕疵。因此，僅髮線加工，亦可確認 易區別功能缺陷的效果。 另外，僅髮線加工時，由於除去量少時，無法防止 生黑色線條，僅端銑刀加工、或端銑刀加工+髮線加工 由 細 處 產 元 滑 而 得 3 c 分 於 處 實 工 疵 瑕 可 容 產 時 -36- 1355301 ，由於除去量適當，確認可防止黑色線條產生。而且，由 3e所形成的鋁合金厚板，於漿料造塊時沒有使用鑄塊微細 化劑之Ti-B時，沒有受到表面平滑化處理之方法的不同處 所影響，確認表面平滑化處理之方法皆可防止黑色線條產 生。 沒有實施平滑化的鋁合金熱延板，會囤積加工變形情 形，在壓延方向之翹曲情形變大，平坦性不佳。而且，板 厚精度與相同組成之鋁合金厚板相比，大多數稍微不佳。 另外，因瑕疵及黑色線條之表面性質不佳。此外，僅髮線 加工之平坦度的値及切斷板之板厚精度的評估，與鋁熱延 板（沒有平滑化處理）之平坦度的値及切斷板之板厚精度 之評估値大約相同（加工代工爲2〜3 μιη，由於經囤積的加 工變形沒有被減輕，在壓延方向之翹曲情形變大、平坦性 變得不佳）。 [實施例2 :供試材料製作] (Al-Mg-Si系合金） 使表4所示之合金No.6a〜6g之組成的鋁合金熔解，且 進行脫氫處理、過濾後，予以鑄造，製作板厚5 00rhm之鑄 塊。使該鑄塊進行熱間壓延處理，製作厚度約25mm、與 厚度約20 mm之鋁合金熱延板。使該鋁合金熱延板切成壓 延方向長度2 00 0mmx寬度1000mm後，對壓延面（兩面）而 言進行平滑化處理，形成厚度2 0mm之鋁合金厚板（切斷 板）。而且，有關含有Ti者，爲防止鑄塊破裂情形時，添 -37- 1355301 加Ti-B母合金。平滑化處理係以端銑刀加工、端銑刀加工 +髮線加工（藉由帶式硏磨不織布）、髮線加工等3種方法 比較其效果。而且，實施端銑刀加工者，係使用厚度約爲 2 5 mm之鋁合金熱延板，且僅實施髮線加工者，係使用厚 度約20mm之鋁合金熱延板。而且，有關端銑刀加工、髮 線加工的方法，與前述Al-Mg系合金時相同。此外，使所 得的鋁合金厚板在52 0°C下進行熔體化處理，在175 °C下實 施時效處理8小時。 (Al-Zn-Mg系合金）Is] After the acid-resistant aluminum treatment mm 0 0 0 o 0 oo O 0 0 ooo 1 XX o XXO 〇oo 0 0 X 〇 酞 _ XXXXXXXXXXXXX 1 XXXXXXX o XXXX 〇Aluminum alloy thermal extension board due to the surface nature of the shelter XXXXXXXXXXXXX 1 XXXXXXXXXXXXX Strength (N/mm2) Endurance S CO Ο CO CQ S in σ> CM in wear this Csi CM Ln CNJ O) 1 CO co S CNJ in Word•^· sm in 00 in s u&gt;ir&gt; Tensile strength CM CVJ CM CM esj σ&gt; C4 o 00 &lt;0 CO 00 σ&gt; CVJ a&gt; CM CO &lt;y&gt; cvi g CO CM O) ow Lft 卜 1 CM σ&gt; CM 0 01 CvJ 00 Oi CM CM another 09 CO CM co a&gt; CM ¢0 00 ¢0 O) 0 CM »· Η Accuracy ◎ ◎ 0 o 0 ◎ oo 0 o ◎ o ◎ 1 ◎ o 〇 ◎ o 〇〇 ◎ ◎ 0 ◎ 0 ◎ Death degree (mm/m) 〇0.42 | 0.50 | 1 0.62 1 0.69 I 1 047 j 0.48 1 Q-47 | 0.50 0.48 0.43 0.49 1 0.42 1 0.48 1 0.50 1 0.49 1 0.48 1 0.48 1 1 0.50 1 0.50 1 0.40 〇1 0.42 〇1 0.44 0 Aluminium Alloy slabs are smoothed by hairline processing and treated with acid-resistant aluminum. The surface properties of the stains are 0 O 0 O 0 〇0 o o OO 〇O 1 XX 〇XXOOO 〇〇〇X 0 骧 but mM coffee XXXXXXXXXXXXX ] XXXXXXX 0 XXXX 0 Because of the surface properties 0 〇oo 0 o 0 o 〇0 o 〇o 1 〇〇o 〇〇〇〇0 〇 〇0 0 0 1 a Accuracy ◎ ◎ 0 o 0 ◎ 0 o 〇0 ◎ 〇 ◎ 1 ◎ 0 o ◎ ooo ◎ ◎ 0 ◎ 0 ◎ Μ (mm/m) 〇O 0.50 I to o 0.68 1 0.47 | 0.48 | i 0-47 | i 0.49 1 0.46 0.43 0.48 1 0-42 1 1 1 0.48 1 0.50 1 0.48 ! 1 0.48 1 0.47 1 0.50 1 0.49 1 0.40 〇5 0 0 1 0.43 0 Alloy 6 ¢0 m 5 in 5 ίο In io in 55 1 5m*| 1 5n * 5o * in 箐5r ♦ 5s * 箐\Ά 1 5u * l〇«〇CO &lt;0 1 3c * 3d* Φ CO 囫 囫面面面* -34- 1355301 The aluminum alloy thick plate formed of Alloy Nos. 5a to 51 and 5v has an appropriate content in the range of the additive element, and is subjected to appropriate smoothing treatment on the surface, strength, flatness, thickness accuracy, and surface. Good quality. Moreover, sufficient strength and good surface properties can be obtained when compared with an aluminum alloy heat-expanding plate which is not subjected to smoothing. On the other hand, in the aluminum alloy thick plate formed of Alloy No. 5m, since the Mg content is insufficient, sufficient strength cannot be obtained. Further, in the aluminum alloy thick plate formed of the alloy Νο·5η, when the Mg content is excessive, casting cracking occurs, and the test material cannot be produced. The aluminum alloy thick plate formed of alloy No. 5o, 5p, 5r, and 5s has a large intermetallic compound due to excessive content of Si, Fe, Μ, and Cr, and the surface appearance after the alumite treatment is Produces a stain. The aluminum alloy thick plates formed of alloy No. 5q, 5t, and 5u have a content of Cu, Zn, and Ti which are each larger than an appropriate range, and compared with alloys No. 5f, 5j, and 5c in which the elements are in an appropriate range. At the time, there is no effect of improving the strength and surface properties. In addition, when the method of the surface smoothing treatment differs, it is possible to confirm the improvement factor when the end mill processing + hairline processing or the end mill processing is performed in an appropriate amount, compared with the hair removal processing with a small amount of removal. The surface properties of cockroaches. Further, there is a flaw in the cut plate of the conventional heat-expanding plate, and it is judged by a small flaw which has no problem of visually observing the visible size, and the flaw seen on the cut plate which is only subjected to the hairline processing, You can visually judge the flaws. Therefore, it is also possible to confirm the effect of easily distinguishing the functional defects only by the hairline processing. In addition, when only the wire is processed, it is impossible to prevent the occurrence of black lines when the amount of removal is small, and only the end mill processing, or the end mill processing + the hairline processing -35-1355301, it is confirmed that the black can be prevented due to the appropriate removal amount. Lines are produced. Moreover, the aluminum alloy thick plate formed by 5 v is not affected by the difference in the method of surface smoothing treatment when the slurry ingot is not used with Ti-B of the ingot micro-chemical agent, and the surface smoothing treatment is confirmed. The method can prevent the blue line from being formed. The aluminum alloy thick plate formed by the alloy No. 3a, 3b, and 3e has a content of the added element in an appropriate range, and is subjected to appropriate flattening treatment on the surface, strength and flatness. , plate thickness accuracy, and surface properties are good. Further, when compared with an aluminum alloy heat-expanding plate which is not subjected to the smoothing treatment, sufficient strength and good surface properties can be obtained. On the other hand, in the aluminum alloy thick plate formed of the alloy No, since the content of Μη is insufficient, the charging strength cannot be obtained. Further, in the aluminum alloy thick plate formed of the alloy No. 3d, since the content of Μη is excessive, a coarse intermetallic compound is formed, and a stain on the surface appearance after the alumite treatment is generated. Moreover, the difference in the method of the surface smoothing treatment is compared with the hairline processing in which only a small amount of removal is performed, when the end mill having the appropriate amount of removal is added + the hairline processing, or when only the end mill processing is performed, Confirm that the surface properties of the crucible are increased. Further, on the cutting plate of the conventional heat-expanding plate, there is a flaw which is determined by a small flaw which has a function of visually observing the visible size, and only the flaw seen on the cutting plate of the hairline processing is performed. Visually judge the flaws. Therefore, only the hairline processing can confirm the effect of easily distinguishing the functional defects. In addition, only the hairline processing, because the amount of removal is small, can not prevent the production of black lines, only the end mill processing, or end mill processing + hairline processing from the fine parts of the production slip 3 c points in the work疵瑕 can be produced at -36-1355301, because the amount of removal is appropriate, it is confirmed that black lines can be prevented. Further, when the aluminum alloy thick plate formed of 3e is used without the use of the ingot refining agent Ti-B at the time of slurry formation, it is not affected by the difference in the surface smoothing treatment method, and the surface smoothing treatment is confirmed. The method can prevent black lines from being generated. The aluminum alloy heat-expanding plate which is not subjected to smoothing will be hoarded and deformed, and the warpage in the rolling direction becomes large, and the flatness is not good. Moreover, the plate thickness accuracy is mostly slightly poor compared to the same composition of aluminum alloy slabs. In addition, the surface properties of the enamel and black lines are not good. In addition, only the flatness of the hairline processing and the evaluation of the sheet thickness accuracy of the cut sheet, and the flatness of the aluminum heat spreader (without smoothing) and the evaluation of the sheet thickness accuracy of the cut sheet are approximated. The same (the processing foundry is 2 to 3 μm, since the warpage deformation due to the entanglement is not alleviated, the warpage in the rolling direction becomes large, and the flatness becomes poor). [Example 2: Preparation of test material] (Al-Mg-Si-based alloy) The aluminum alloy having the composition of Alloy No. 6a to 6g shown in Table 4 was melted, dehydrogenated, filtered, and cast. Make an ingot with a thickness of 500 rpm. The ingot was subjected to hot rolling treatment to prepare an aluminum alloy heat-expanding plate having a thickness of about 25 mm and a thickness of about 20 mm. After the hot-rolled aluminum alloy sheet was cut into a length of 200 mm in the rolling direction and a width of 1000 mm, the calendered surface (both sides) was smoothed to form an aluminum alloy thick plate (cutting plate) having a thickness of 20 mm. Moreover, in the case of containing Ti, in order to prevent the ingot from breaking, add -37-1355301 plus Ti-B master alloy. The smoothing process compares the effects of end mill milling, end milling machining + hairline machining (by belt honing non-woven fabric) and hairline machining. Moreover, the end mill cutter is to use an aluminum alloy heat-expanding plate having a thickness of about 25 mm, and only a hairline processor is used, and an aluminum alloy heat-expanding plate having a thickness of about 20 mm is used. Further, the method of processing the end mill and the wire processing are the same as those of the aforementioned Al-Mg alloy. Further, the obtained aluminum alloy thick plate was subjected to melt treatment at 52 ° C, and aging treatment was carried out at 175 ° C for 8 hours. (Al-Zn-Mg alloy)

使表4所示之合金No.7a〜7g之組成的銘合金熔解，且 進行脫氫處理、過濾後，予以鑄造，製作板厚5 00mm之鑄 塊。使該鑄塊進行熱間壓延處理，製作厚度約2 5mm、與 厚度約20mm之鋁合金熱延板。使該鋁合金熱延板切成壓 延方向長度2000mmx寬度1 000mm後，對壓延面（兩面）而 言進行平滑化處理，形成厚度2 0 mm之鋁合金厚板（切斷 板）。而且，有關含有Ti者，爲防止鑄塊破裂情形時，添 加Ti-B母合金。平滑化處理係以端銑刀加工、端銑刀加工 +髮線加工（藉由帶式研磨不織布）、髮線加工等3種方法 比較其效果。而且，實施端銑刀加工者，係使用厚度約爲 2 5 mm之鋁合金熱延板，且僅實施髮線加工者，係使用厚 度約20mm之鋁合金熱延板。此外，有關端銑刀加工、髮 線加工之方法，係與前述Al-Mg系合金時相同。另外，使 所得的鋁合金厚板在470°C下進行熔體化處理，且在120°C -38- 1355301 下實施時效處理48小時。 【表4】 合金 鋁合金成分賊質量％) No. Mg Si Fe Cu Μη Cr Zn Ti Zr Al** 6a 0.9 0.5 0.5 0.3 0.1 0.2 0.2 0.02 — 殘留成分 6b 0.5 0.9 0.2 - 0.1 - - 0.02 — 殘留成分 6c * 0.9 0.1* 0.5 - 0.1 擎 - 0.02 - 殘留成分 6d* 0.9 1.8* 0.4 - 0.1 - — 0.02 - 殘留成分 6e * 0.2* 0.5 0.5 - 0.1 - - 0.02 — 贿成分 6f* 1.7* 0.5 0.4 - 0.1 - - 0.02 — a留齡 6g 0.9 0.5 0.5 0.3 0.1 0.2 0.2 — - 贿成分 7a 2.5 0.1 0.2 1.8 - 0.2 4.0 0.02 — 殘留成分 7b 3.5 0.2 0.2 2.0 - 8.0 0.02 0.2 殘留成分 7c * 0.3* 0.1 0.2 2.2 - 0.1 4.0 0.02 a留成i 7d， 5.0* 0.2 0.2 2.0 - 0.1 5.0 0.02 — 殘留成分 7e * 2.5 0.1 0.2 2.2 - 0.1 2.4* 0.02 - a留成分 /t&gt; 3.0 0.2 0.2 2.0 - 0.1 9.5* 0.02 — i留齡 7g 2.5 0.1 0.2 1.8 - 0.2 4.0* — - 殘留成分 :適當範圍外 含有不可避免的雜質The alloy of the composition of the alloy No. 7a to 7g shown in Table 4 was melted, dehydrogenated, filtered, and cast to prepare an ingot having a thickness of 500 mm. The ingot was subjected to hot rolling treatment to prepare an aluminum alloy heat-expanding plate having a thickness of about 25 mm and a thickness of about 20 mm. After the hot-rolled aluminum alloy sheet was cut into a length of 2000 mm in the rolling direction and a width of 1 000 mm, the calendered surface (both sides) was smoothed to form an aluminum alloy thick plate (cutting plate) having a thickness of 20 mm. Further, in the case of containing Ti, in order to prevent the ingot from being broken, a Ti-B mother alloy is added. The smoothing process compares the effects of end mill milling, end milling machining + hairline machining (by belt polishing non-woven fabric) and hairline processing. Moreover, the end mill cutter is to use an aluminum alloy heat-expanding plate having a thickness of about 25 mm, and only a hairline processor is used, and an aluminum alloy heat-expanding plate having a thickness of about 20 mm is used. In addition, the method of processing the end mill and the processing of the wire are the same as those of the aforementioned Al-Mg alloy. Further, the obtained aluminum alloy thick plate was subjected to a melt treatment at 470 ° C, and an aging treatment was carried out at 120 ° C - 38 - 1355301 for 48 hours. [Table 4] Alloy aluminum alloy composition thief mass%) No. Mg Si Fe Cu Μη Cr Zn Ti Zr Al** 6a 0.9 0.5 0.5 0.3 0.1 0.2 0.2 0.02 — Residual component 6b 0.5 0.9 0.2 - 0.1 - - 0.02 — Residual component 6c * 0.9 0.1* 0.5 - 0.1 擎 - 0.02 - Residual component 6d* 0.9 1.8* 0.4 - 0.1 - 0.02 - Residual component 6e * 0.2* 0.5 0.5 - 0.1 - - 0.02 - Bribe component 6f* 1.7* 0.5 0.4 - 0.1 - - 0.02 - a 6 years of age 0.9 0.5 0.5 0.3 0.1 0.2 0.2 — - Bribe ingredients 7a 2.5 0.1 0.2 1.8 - 0.2 4.0 0.02 — Residual composition 7b 3.5 0.2 0.2 2.0 - 8.0 0.02 0.2 Residual component 7c * 0.3* 0.1 0.2 2.2 - 0.1 4.0 0.02 a retained i 7d, 5.0* 0.2 0.2 2.0 - 0.1 5.0 0.02 — Residual component 7e * 2.5 0.1 0.2 2.2 - 0.1 2.4* 0.02 - a retention component / t &gt; 3.0 0.2 0.2 2.0 - 0.1 9.5* 0.02 — i stay Age 7g 2.5 0.1 0.2 1.8 - 0.2 4.0* — - Residual composition: Inevitable impurities outside the appropriate range

[實施例2 :評估] 在所得的鋁合金厚板上，與實施例1相同的方法進行 強度及表面性質之評估，結果如表5,6所示。而且，亦製 作沒有實施平滑化處理的鋁合金熱延板（厚度爲20mm ) ，以相同的條件實施熔體化處理及時效處理，作爲比較例 予以評估。強度之合格基準，合金No.6a〜6g(Al〜Mg〜 Si系合金），拉伸強度爲2 0 0N/mm2以上、合金No.7a〜7g (Al-Zn-Mg系合金），拉伸強度爲2 5 0N/mm2以上。 而且，端銑刀加工+髮線加工、及僅髮線加工之強度 的値，由於與僅端銑刀加工之強度的値相同，故於表中省 略記載。 -39- 1355301 【表5】[Example 2: Evaluation] Evaluation of strength and surface properties was carried out in the same manner as in Example 1 on the obtained aluminum alloy thick plate, and the results are shown in Tables 5 and 6. Further, an aluminum alloy heat-expanding plate (thickness: 20 mm) which was not subjected to the smoothing treatment was also produced, and the melt treatment and the aging treatment were carried out under the same conditions, and were evaluated as comparative examples. For the strength criteria, Alloy No. 6a to 6g (Al to Mg to Si alloy), tensile strength of 200 N/mm2 or more, alloy No. 7a to 7 g (Al-Zn-Mg alloy), and stretching The strength is 2 50 N/mm 2 or more. Further, the strength of the end mill processing + hairline processing and the strength of the hairline only processing is the same as that of the strength of the end mill processing only, and therefore is omitted in the table. -39- 1355301 [Table 5]

合金 No. 鋁合金厚板 藉由端銳刀加工之平滑化處理 藉由端銳刀加工+髮線加工之 平滑化處理 強度(N/mm2) 酎酸銘處理後 耐_處理後 拉伸強度 耐力 因瑕庇之 表面性質 因黒色線條 之表面性質 因色斑之 表面性質 因瑕疵之 表面ttS 因黑色線條 之表面性質 因色斑之 表面性質 6a 323 274 ◎ 〇 〇 ◎ 〇 〇 6b 292 249 ◎ 〇 〇 ◎ 〇 〇 6c * 115 67 ◎ 〇 〇 ◎ 〇 〇 6d* 336 298 ◎ 〇 X ◎ 〇 X 6e * 174 121 ◎ 〇 〇 ◎ 〇 〇 6&quot; 210 124 ◎ 〇 〇 ◎ 〇 〇 6s 321 273 ◎ 〇 〇 ◎ 〇 〇 7a 424 364 ◎ 〇 〇 ◎ 〇 〇 7b 511 450 ◎ 〇 〇 ◎ 〇 〇 7c * 195 168 ◎ 〇 〇 ◎ 〇 〇 7d* 289 190 ◎ 〇 X ◎ 〇 X 7e* 212 132 ◎ 〇 〇 ◎ 〇 〇 7f &gt;* 610 530 ◎ 〇 X ◎ 〇 X 7r 423 363 ◎ 〇 X ◎ 〇 X *:適當範圍外 【表6】Alloy No. Aluminium alloy thick plate is smoothed by end sharp knife processing. Smoothing treatment strength (N/mm2) by end sharp knife processing + hairline processing. Due to the surface nature of the ruthenium due to the surface properties of the ochre line due to the surface properties of the plaque due to the surface ttS due to the surface properties of the black line due to the surface properties of the plaque 6a 323 274 ◎ 〇〇 ◎ 〇〇 6b 292 249 ◎ 〇〇 ◎ 〇〇6c * 115 67 ◎ 〇〇 ◎ 〇〇 6d* 336 298 ◎ 〇 X ◎ 〇 X 6e * 174 121 ◎ 〇〇 ◎ 〇〇 6 &quot; 210 124 ◎ 〇〇 ◎ 〇〇 6s 321 273 ◎ 〇〇 ◎ 〇〇7a 424 364 ◎ 〇〇 ◎ 〇〇 7b 511 450 ◎ 〇〇 ◎ 〇〇 7c * 195 168 ◎ 〇〇 ◎ 〇〇 7d* 289 190 ◎ 〇 X ◎ 〇 X 7e* 212 132 ◎ 〇〇 ◎ 〇〇 7f &gt;* 610 530 ◎ 〇X ◎ 〇X 7r 423 363 ◎ 〇X ◎ 〇X *: Out of range [Table 6]

合金 No. 鋁合金厚板 鋁合金熱延板 藉由髮線加工之平滑化處理 耐酸鋁處理厚 強度(N/mm2) 耐酸銘處理厚 因瑕疵之 表面性質 因黑線條之 表面性質 因色斑之 表面性質 拉伸強度 耐力 因瑕疵之 表面性質 因黑線條之 表面性質 因色斑之 表面性質 6a 〇 X 〇 342 269 X X 〇 6b 〇 X 〇 315 271 X X 〇 6c * 〇 X 〇 137 88 X X 〇 6d* 〇 X X 364 324 X X X 6e * 〇 X 〇 198 142 X X 〇 6f * 〇 X 〇 234 145 X X 〇 6k 〇 〇 〇 340 268 X 〇 〇 7a 〇 X 〇 439 378 X X 〇 7b 〇 X 〇 531 471 X X 〇 7c * 〇 X 〇 208 171 X X 〇 7d* 〇 X X 301 200 X X X 7e* 〇 X 〇 222 144 X X 〇 7f * 〇 X X 612 531 X X X 7g 〇 〇 X 437 376 X 〇 X 適當範圍外 由合金No.6a,6b，6 g所形成的鋁合金厚板，添加元素之 含量爲適當的範圍內，由於在表面上實施適當的平滑化處 理，強度及表面性質佳。而且，與沒有實施平滑化處理的 -40- 1355301 鋁合金熱延板相比時，可得充分的強度及良好的表面性質 。對此而言，由合金No. 6c,6e所形成的鋁合金厚板，由於 Si, Mg之各含量不足，無法得到充分的強度。另外，由合 金No.6d所形成的鋁合金厚板，由於Si含量過剩時，會形 成粗大的金屬間化合物，在耐酸鋁處理後之表面外觀上產 生色斑。而且，由合金No .6 f所形成的鋁合金厚板，由於 Mg之含量過剩，由於形成Al-Mg系（ 5 000系A1)合金之特 性，藉由熔體化處理及時效處理，無法得到提高強度的效 果’與Mg之含量在適當範圍內之合金No.6a,6b相比時，會 有強度降低的情形。 此外，有關表面平滑化處理之方法不同處，與除去量 少之僅髮線加工處理相比時，除去量適當的端銑刀加工+ 髮線加工、或僅端銑刀加工時，可確認提高因瑕疵之表面 性質。而且，在習知的熱延板之切斷板上有瑕疵，包含以 肉眼觀察可見的尺寸之功能完全沒有問題的微小瑕疵所判 斷者，僅實施髮線加工之切斷板上所見的瑕疵，可以目視 明顯判斷的瑕疵。因此，即使僅髮線加工處理，仍可確認 容易區別功能缺陷的效果。 另外，僅髮線加工處理時，由於除去量少時，無法防 止產生黑色線條，僅端銑刀加工處理、或端銑刀加工+髮 線加工時，由於除去量適當，確認可防止黑色線條產生。 而且，由6g所形成的鋁合金厚板，於漿料造塊時沒有使用 鑄塊微細化劑之Ti-B時，沒有受到表面平滑化處理之方法 的不同處所影響，確認表面平滑化處理之方法皆可防止黑 -41 - 1355301 色線條產生。 由合金No.7a、7b、7g所形成的鋁合金厚板，添力D元 素之含量爲適當的範圍內，由於在表面上實施適當的平滑 化處理，強度及表面性質良好。而且，與沒有實施平滑化 處理的鋁合金熱延板相比時，可得充分的強度及良好的表 面性質。對此而言，由合金No. 7c，7e所形成的鋁合金厚板 ，由於Mg，Zn之含量不足，無法得到充分的強度。另外， 由合金No.7d，7f所形成的鋁合金厚板，由於Mg,Zn之含量 過剩，會形成粗大的金屬間化合物，在耐酸鋁處理後之表 面外觀上產生色斑。 而且，有關表面平滑化處理之方法的不同處，與僅實 施除去量少的髮線加工相比時，除去量適當的端銑刀加工 處理+髮線加工、或僅實施端銑刀加工時，可確認提高因 瑕疵之表面性質。而且，在習知的熱延板之切斷板上有瑕 疵，包含以肉眼觀察可見的尺寸之功能完全沒有問題的微 小瑕疵所判斷者，僅實施髮線加工處理之切斷板上所見的 瑕疵，可以目視明顯判斷的瑕疵。因此，即使僅髮線加工 ，仍可確認容易區別功能缺陷的效果。 另外，僅髮線加工時，由於除去量少時，無法防止產 生黑色線條，僅端銑刀加工、或端銑刀加工+髮線加工時 ，由於除去量適當，確認可防止黑色線條產生。而且，由 7g所形成的鋁合金厚板，於漿料造塊時沒有使用鑄塊微細 化劑之Ti-B時，沒有受到表面平滑化處理之方法的不同處 所影響，確認表面平滑化處理之方法皆可防止黑色線條產 -42- 1355301 生。 如上述說明可知，本發明之鋁合金熱厚板，具有良好 的平坦性及板厚精度，同時可抑制因瑕疵及黑色線條之表 面缺陷，具有良好的表面性質。而且，可知藉由使各種合 金之成分組成爲適當之値，可提高強度等之特性，且可抑 制表面之色斑，表面性質更佳者。 【圖式簡單說明】 [第1圖]係爲本發明之鋁合金厚板的製造方法之流程圖 〇 [第2圖]係爲習知技術之鋁合金厚板的製造方法例之流 程圖。 . &quot; -43-Alloy No. Aluminum alloy thick plate Aluminum alloy hot-dip sheet is smoothed by hairline processing. Alumina-resistant thickening strength (N/mm2) Acid-resistant treatment of thick surface due to the surface properties of black lines due to color spots Surface properties Tensile strength endurance due to the surface properties of the surface due to the surface properties of the black lines due to the surface properties of the stains 6a 〇X 〇342 269 XX 〇6b 〇X 〇315 271 XX 〇6c * 〇X 〇137 88 XX 〇6d* 〇 XX 364 324 XXX 6e * 〇X 〇198 142 XX 〇6f * 〇X 〇234 145 XX 〇6k 〇〇〇340 268 X 〇〇7a 〇X 〇439 378 XX 〇7b 〇X 〇531 471 XX 〇7c * 〇X 〇208 171 XX 〇7d* 〇XX 301 200 XXX 7e* 〇X 〇222 144 XX 〇7f * 〇XX 612 531 XXX 7g 〇〇X 437 376 X 〇X Out of range by alloy No.6a,6b, The aluminum alloy thick plate formed by 6 g has an additive element content within an appropriate range, and is excellent in strength and surface properties by performing appropriate smoothing treatment on the surface. Moreover, sufficient strength and good surface properties can be obtained when compared with the -40-1355301 aluminum alloy heat-expanding plate which is not subjected to the smoothing treatment. On the other hand, in the aluminum alloy thick plate formed of Alloy No. 6c, 6e, since the content of each of Si and Mg is insufficient, sufficient strength cannot be obtained. Further, in the aluminum alloy thick plate formed by the alloy No. 6d, when the Si content is excessive, a coarse intermetallic compound is formed, and the surface appearance of the alumite treatment results in a color unevenness. Further, since the aluminum alloy thick plate formed of the alloy No. 6 f is excessive in content of Mg, the characteristics of the Al-Mg-based (5,000-series A1) alloy are formed, and it is impossible to obtain a melt treatment and a aging treatment. The effect of improving the strength is such that the strength is lowered when compared with the alloy No. 6a, 6b in which the content of Mg is within an appropriate range. In addition, when the method of the surface smoothing treatment differs from the hairline processing with a small amount of removal, it is confirmed that the end mill processing + hairline processing or the end milling cutter processing is performed when the removal amount is appropriate. Because of the surface properties. Further, in the conventional hot-rolled plate, there is a crucible, and it is judged by a small flaw which has no problem in visually observing the visible size, and only the flaw seen on the cut sheet of the hairline processing is performed. You can visually judge the flaws. Therefore, even if only the hairline processing is performed, it is possible to confirm the effect of easily distinguishing the functional defects. In addition, in the hairline processing only, when the amount of removal is small, black lines cannot be prevented from being generated, and only the end mill processing or the end mill processing + hairline processing is performed, and it is confirmed that the black line is prevented due to the appropriate removal amount. . Further, when the aluminum alloy thick plate formed of 6 g is used without the use of the ingot refining agent Ti-B at the time of slurry formation, it is not affected by the difference in the surface smoothing treatment method, and the surface smoothing treatment is confirmed. The method can prevent black-41 - 1355301 color lines from being generated. The aluminum alloy thick plate formed of the alloy Nos. 7a, 7b, and 7g has a content of the added force D element in an appropriate range, and is subjected to an appropriate smoothing treatment on the surface to have good strength and surface properties. Further, when compared with an aluminum alloy heat-expanding plate which is not subjected to the smoothing treatment, sufficient strength and good surface properties can be obtained. On the other hand, in the aluminum alloy thick plate formed of Alloy No. 7c, 7e, since the content of Mg and Zn is insufficient, sufficient strength cannot be obtained. Further, in the aluminum alloy thick plate formed of Alloy No. 7d, 7f, since the content of Mg and Zn is excessive, a coarse intermetallic compound is formed, and a stain on the surface of the surface after the alumite treatment is generated. Further, in the difference in the method of the surface smoothing treatment, when the end milling cutter processing + hairline processing is performed, or only the end milling cutter processing is performed, when the hair removal processing with only a small amount of removal is performed, It can be confirmed that the surface properties of the crucible are improved. Further, there is a crucible on a cutting plate of a conventional heat-expanding plate, and it is judged by a small flaw which has no problem in that the function of visually observing the visible size is completely solved, and only the crucible seen on the cutting board which is subjected to the hairline processing is performed. You can visually judge the flaws. Therefore, even if only the hairline processing is performed, the effect of easily distinguishing the functional defects can be confirmed. Further, in the hairline processing only, when the amount of removal is small, it is impossible to prevent the occurrence of black lines, and only the end mill processing or the end mill processing + hairline processing is performed, and it is confirmed that the black line is prevented due to the appropriate amount of removal. Further, when the aluminum alloy thick plate formed of 7 g is used without the use of the ingot refining agent Ti-B at the time of slurry formation, it is not affected by the difference in the surface smoothing treatment method, and the surface smoothing treatment is confirmed. The method can prevent the black line from producing -42-1355301. As apparent from the above description, the aluminum alloy hot plate of the present invention has good flatness and plate thickness precision, and can suppress surface defects due to flaws and black lines, and has good surface properties. Further, it has been found that by making the components of various alloys suitable, the properties such as strength can be improved, and the surface unevenness can be suppressed, and the surface properties are better. [Brief Description of the Drawings] [Fig. 1] is a flow chart showing a method for producing an aluminum alloy thick plate according to the present invention. [Fig. 2] is a flow chart showing an example of a method for producing an aluminum alloy thick plate of the prior art. . &quot; -43-

Claims (1)

1356301 第098110134號專利申請案中文申請專利範圍修正本 - 民國100年7月13日修正 七、申請專利範圍： L —種銘合金厚板，其係爲使鋁合金熱間壓延板之表 面予以平滑化所形成的鋁合金厚板，其特徵爲表面之平坦 度在每lm之壓延方向長度爲〇.2mm以下，板厚之不均勻性 在企求的板厚±0.5 %以內。 2. 如申請專利範圍第1項之銘合金厚板，其中係由含 . 有Mg: 1.5〜12.0質量％ '及含有1種以上之Si: 〇.7質量％ 以下、Fe : 0.8質量％以下、Cu : 0.6質量％以下、Μη : 1.0 質量％以下、C r : 0.5質量％以下、Ζη : 〇 . 4質量％以下、Ti :〇.1質量％以下，且殘留成分爲A1及不可避免的雜質所形 成的銘合金所形成。 3. 如申請專利範圍第1項之鋁合金厚板，其中係由含 有Μη : 0.3〜1.6質量％、及含有1種以上之Si : 0.7質量％以 下、Fe : 〇.8質量％以下、Cu : 0.5質量％以下、Mn : 1 _5質 量％以下、C r : 0.3質量％以下、Ζ η : 0 · 4質量％以下、T i : 〇.1質量％以下，且殘留成分爲A1及不可避免的雜質所形成 的鋁合金所形成。 4. 如申請專利範圍第1項之錫合金厚板’其中係由含 有Mg: 0.3〜1.5質量％、Si: 0.2〜1.6質量°/〇、及含有1種 以上之Fe : 〇.8質量％以下、Cu : 1.〇質量％以下、Μη : 0.6 質量％以下、c r : 0 · 5質量％以下、Ζ η : 〇 ·4質量°/°以下、T i :0.1質量％以下，且殘留成分爲A1及不可避免的雜質所形 1355301 成的鋁合金所形成。 5. 如申請專利範圍第1項之鋁合金厚板’其中係由含 有Zn: 3.0〜9.0質量％、Mg: 0.4〜4_0質量％、及含有1種 以上之S i : 0 · 7質量％以下、F e : 0.8質量％以下、C u : 3 _ 0 質量％以下、Μη : 0.8質量％以下、Cr : 0.5質量％以下、Ti :0.1質量％以下、Zr : 〇_25質量％以下，且殘留成分爲A1 及不可避免的雜質所形成的鋁合金所形成。 6. —種鋁合金厚板之製造方法，其係爲申請專利範圍 第1項之鋁合金厚板的製造方法，其特徵爲進行使鋁合金 熔融、形成鋁合金熔湯之熔融步驟，與自前述鋁合金熔湯 中除去氫氣之脫氫步驟，與自除去氫氣之鋁合金熔湯中除 去中間物的過濾步驟，與使前述除去中間物之鋁合金熔湯 予以鑄造以製造鑄塊的鑄造步驟，與使前述鑄塊予以熱間 壓延成所定厚度，製造熱間壓延板之熱間壓延步驟，與切 斷前述熱間壓延板，形成所定的壓延方向長度及寬度的切 斷步驟’與使前述經切斷的熱間壓延板之表面予以平滑化 的平滑化處理步驟， 於前述平滑化處理步驟中，前述熱間壓延板表面之除 去厚度係每一面爲2〜5mm。 7. 如申請專利範圍第6項之鋁合金厚板的製造方法， 其中於則述之熱間壓延步驟前，藉由使前述鑄塊在4〇〇。匚 以上、未達前述鋁合金之熔點下進行熱處理1小時以上， 進行均熱處理步驟。 8.如申請專利範圍第6項之鋁合金厚板的製造方法 工严01 其中於前述之平滑化處理步驟前，進行使前述經切斷的熱 間壓延板予以退火（annealing )的退火步驟。 9. 如申請專利範圍第6項之鋁合金厚板的製造方法， 其中前述平滑化處理步驟係藉由切削法、硏削法、及硏磨 法中任何一種以上的方法進行。 10. 如申請專利範圍第6項之鋁合金厚板的製造方法， 其中前述鋁合金係爲申請專利範圍第2〜5項中任—項之銘 合金。 -3-1356301 Patent Application No. 098110134 Revision of Chinese Patent Application Scope - Amendment of July 13, 100, Republic of China VII. Application Patent Range: L—Ming Ming alloy thick plate, which is to smooth the surface of aluminum alloy hot rolled sheet The aluminum alloy thick plate formed by the method is characterized in that the flatness of the surface is less than 2 mm in the rolling direction per lm, and the unevenness of the thickness is within ±0.5% of the desired thickness. 2. For example, the alloy thick plate of the first application of the patent scope includes: Mg: 1.5 to 12.0% by mass ' and more than one type of Si: 〇.7 mass% or less, Fe: 0.8 mass% or less Cu: 0.6% by mass or less, Μη: 1.0% by mass or less, Cr: 0.5% by mass or less, Ζη: 〇. 4% by mass or less, Ti: 〇.1% by mass or less, and the residual component is A1 and unavoidable Formed by the alloy formed by impurities. 3. The aluminum alloy thick plate according to the first aspect of the patent application, which contains Μη: 0.3 to 1.6% by mass, and one or more kinds of Si: 0.7% by mass or less, Fe: 〇.8% by mass or less, Cu : 0.5% by mass or less, Mn: 1 _5 mass% or less, C r : 0.3 mass% or less, Ζ η : 0 · 4 mass% or less, T i : 〇.1 mass% or less, and the residual component is A1 and inevitably The aluminum alloy formed by the impurities is formed. 4. The tin alloy thick plate of the first application of the patent scope includes: Mg: 0.3 to 1.5% by mass, Si: 0.2 to 1.6 mass%/〇, and one or more kinds of Fe: 〇. 8 mass% Hereinafter, Cu: 1.〇% by mass or less, Μη: 0.6% by mass or less, cr: 0·5 mass% or less, Ζ η: 〇·4 mass °/° or less, T i : 0.1% by mass or less, and residual components It is formed of aluminum alloy of 1355301 formed by A1 and unavoidable impurities. 5. The aluminum alloy thick plate of the first aspect of the patent application includes Zn: 3.0 to 9.0% by mass, Mg: 0.4 to 4% by mass, and one or more kinds of S i : 0 · 7 mass% or less. F e : 0.8% by mass or less, C u : 3 _ 0 mass % or less, Μ η : 0.8 mass % or less, Cr: 0.5 mass % or less, Ti: 0.1 mass % or less, Zr : 〇 _25 mass % or less, and The residual component is formed of an aluminum alloy formed by A1 and unavoidable impurities. 6. A method for producing an aluminum alloy thick plate, which is a method for producing an aluminum alloy thick plate according to claim 1 of the patent application, characterized in that a melting step of melting an aluminum alloy to form an aluminum alloy melt is performed, and a dehydrogenation step of removing hydrogen gas in the aluminum alloy melt, a filtration step of removing an intermediate from an aluminum alloy melt from which hydrogen is removed, and a casting step of casting the aluminum alloy melt to remove the intermediate to produce an ingot And the step of heat-calendering the ingot to a predetermined thickness to produce a hot-rolled sheet, and the step of cutting the inter-heat-rolled sheet to form a predetermined length and width in the rolling direction, and The surface of the heat-intercalated sheet that has been cut is subjected to a smoothing and smoothing treatment step. In the smoothing step, the thickness of the surface of the heat-rolled rolled sheet is 2 to 5 mm per side. 7. The method of manufacturing an aluminum alloy slab according to item 6 of the patent application, wherein the ingot is placed at 4 Torr before the hot rolling step.匚 The heat treatment is carried out for 1 hour or more at a melting point of the aluminum alloy as described above, and a soaking step is performed. 8. The method for producing an aluminum alloy slab according to claim 6 s. s. 01. Before the smoothing treatment step described above, an annealing step of annealing the cut hot interlaminar sheet is performed. 9. The method of producing an aluminum alloy slab according to the sixth aspect of the invention, wherein the smoothing treatment step is carried out by any one of a cutting method, a boring method, and a honing method. 10. The method for producing an aluminum alloy slab according to item 6 of the patent application, wherein the aluminum alloy is an alloy of any one of the items 2 to 5 of the patent application. -3-