TW201006578A - Aluminum alloy thick plate and method for manufacturing the same - Google Patents
Aluminum alloy thick plate and method for manufacturing the same Download PDFInfo
- Publication number
- TW201006578A TW201006578A TW98110134A TW98110134A TW201006578A TW 201006578 A TW201006578 A TW 201006578A TW 98110134 A TW98110134 A TW 98110134A TW 98110134 A TW98110134 A TW 98110134A TW 201006578 A TW201006578 A TW 201006578A
- Authority
- TW
- Taiwan
- Prior art keywords
- mass
- aluminum alloy
- less
- thick plate
- thickness
- Prior art date
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 192
- 238000000034 method Methods 0.000 title claims abstract description 55
- 238000004519 manufacturing process Methods 0.000 title claims description 31
- 238000009499 grossing Methods 0.000 claims abstract description 58
- 238000005096 rolling process Methods 0.000 claims abstract description 31
- 238000005520 cutting process Methods 0.000 claims abstract description 27
- 238000005266 casting Methods 0.000 claims abstract description 19
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims abstract description 16
- 238000010438 heat treatment Methods 0.000 claims abstract description 13
- 238000001914 filtration Methods 0.000 claims abstract description 9
- 239000000956 alloy Substances 0.000 claims description 96
- 229910045601 alloy Inorganic materials 0.000 claims description 94
- 239000012535 impurity Substances 0.000 claims description 17
- 238000002844 melting Methods 0.000 claims description 17
- 230000008018 melting Effects 0.000 claims description 15
- 229910052719 titanium Inorganic materials 0.000 claims description 14
- 229910052782 aluminium Inorganic materials 0.000 claims description 13
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 13
- 229910052739 hydrogen Inorganic materials 0.000 claims description 12
- 239000001257 hydrogen Substances 0.000 claims description 12
- 238000003490 calendering Methods 0.000 claims description 9
- 229910052804 chromium Inorganic materials 0.000 claims description 9
- 238000006356 dehydrogenation reaction Methods 0.000 claims description 9
- 238000002161 passivation Methods 0.000 claims description 9
- 229910052748 manganese Inorganic materials 0.000 claims description 5
- 229910052710 silicon Inorganic materials 0.000 claims description 5
- 229910052799 carbon Inorganic materials 0.000 claims description 3
- 229910052726 zirconium Inorganic materials 0.000 claims description 3
- 238000007731 hot pressing Methods 0.000 claims 1
- 229910052746 lanthanum Inorganic materials 0.000 claims 1
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 claims 1
- 230000007547 defect Effects 0.000 abstract description 39
- 238000005098 hot rolling Methods 0.000 abstract description 10
- 239000004065 semiconductor Substances 0.000 abstract description 7
- 238000012937 correction Methods 0.000 abstract description 5
- 238000000137 annealing Methods 0.000 abstract 2
- 238000012545 processing Methods 0.000 description 81
- 230000000694 effects Effects 0.000 description 46
- 239000011701 zinc Substances 0.000 description 25
- 239000000463 material Substances 0.000 description 18
- 239000000203 mixture Substances 0.000 description 17
- 229910018134 Al-Mg Inorganic materials 0.000 description 14
- 229910018467 Al—Mg Inorganic materials 0.000 description 14
- 229910000765 intermetallic Inorganic materials 0.000 description 14
- 239000011347 resin Substances 0.000 description 13
- 229920005989 resin Polymers 0.000 description 13
- 238000011156 evaluation Methods 0.000 description 12
- 238000003754 machining Methods 0.000 description 12
- 238000003801 milling Methods 0.000 description 12
- 239000000047 product Substances 0.000 description 12
- 238000012360 testing method Methods 0.000 description 10
- 229910021365 Al-Mg-Si alloy Inorganic materials 0.000 description 7
- 229910018571 Al—Zn—Mg Inorganic materials 0.000 description 7
- 230000007849 functional defect Effects 0.000 description 7
- 239000004615 ingredient Substances 0.000 description 7
- 238000007670 refining Methods 0.000 description 7
- 238000002791 soaking Methods 0.000 description 7
- 239000003795 chemical substances by application Substances 0.000 description 6
- 230000007797 corrosion Effects 0.000 description 6
- 238000005260 corrosion Methods 0.000 description 6
- 239000004745 nonwoven fabric Substances 0.000 description 6
- 239000002002 slurry Substances 0.000 description 6
- 238000004381 surface treatment Methods 0.000 description 6
- 229910052725 zinc Inorganic materials 0.000 description 6
- 229910018131 Al-Mn Inorganic materials 0.000 description 5
- 229910018461 Al—Mn Inorganic materials 0.000 description 5
- 230000032683 aging Effects 0.000 description 5
- 239000013078 crystal Substances 0.000 description 5
- 229910052742 iron Inorganic materials 0.000 description 5
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 4
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 4
- 238000005336 cracking Methods 0.000 description 4
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 4
- 239000010931 gold Substances 0.000 description 4
- 229910052737 gold Inorganic materials 0.000 description 4
- 239000000155 melt Substances 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 238000007747 plating Methods 0.000 description 4
- 229920006395 saturated elastomer Polymers 0.000 description 4
- 230000035882 stress Effects 0.000 description 4
- 229910000861 Mg alloy Inorganic materials 0.000 description 3
- HEMHJVSKTPXQMS-UHFFFAOYSA-M Sodium hydroxide Chemical compound [OH-].[Na+] HEMHJVSKTPXQMS-UHFFFAOYSA-M 0.000 description 3
- 239000002253 acid Substances 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 238000007689 inspection Methods 0.000 description 3
- 230000014759 maintenance of location Effects 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 230000002441 reversible effect Effects 0.000 description 3
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 2
- 229910019752 Mg2Si Inorganic materials 0.000 description 2
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 239000000853 adhesive Substances 0.000 description 2
- 230000001070 adhesive effect Effects 0.000 description 2
- 238000005054 agglomeration Methods 0.000 description 2
- 230000002776 aggregation Effects 0.000 description 2
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 2
- 239000011248 coating agent Substances 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 229910003460 diamond Inorganic materials 0.000 description 2
- 239000010432 diamond Substances 0.000 description 2
- 239000007888 film coating Substances 0.000 description 2
- 238000009501 film coating Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000009830 intercalation Methods 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 238000009991 scouring Methods 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- SEPPVOUBHWNCAW-FNORWQNLSA-N (E)-4-oxonon-2-enal Chemical compound CCCCCC(=O)\C=C\C=O SEPPVOUBHWNCAW-FNORWQNLSA-N 0.000 description 1
- LLBZPESJRQGYMB-UHFFFAOYSA-N 4-one Natural products O1C(C(=O)CC)CC(C)C11C2(C)CCC(C3(C)C(C(C)(CO)C(OC4C(C(O)C(O)C(COC5C(C(O)C(O)CO5)OC5C(C(OC6C(C(O)C(O)C(CO)O6)O)C(O)C(CO)O5)OC5C(C(O)C(O)C(C)O5)O)O4)O)CC3)CC3)=C3C2(C)CC1 LLBZPESJRQGYMB-UHFFFAOYSA-N 0.000 description 1
- 229910018464 Al—Mg—Si Inorganic materials 0.000 description 1
- 229910018575 Al—Ti Inorganic materials 0.000 description 1
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 1
- 229910052684 Cerium Inorganic materials 0.000 description 1
- ZAMOUSCENKQFHK-UHFFFAOYSA-N Chlorine atom Chemical compound [Cl] ZAMOUSCENKQFHK-UHFFFAOYSA-N 0.000 description 1
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- 244000166124 Eucalyptus globulus Species 0.000 description 1
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 1
- 239000004698 Polyethylene Substances 0.000 description 1
- KJTLSVCANCCWHF-UHFFFAOYSA-N Ruthenium Chemical compound [Ru] KJTLSVCANCCWHF-UHFFFAOYSA-N 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- 229910001128 Sn alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910001297 Zn alloy Inorganic materials 0.000 description 1
- MCMNRKCIXSYSNV-UHFFFAOYSA-N ZrO2 Inorganic materials O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 1
- 238000010306 acid treatment Methods 0.000 description 1
- 229940037003 alum Drugs 0.000 description 1
- 150000004645 aluminates Chemical class 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 229910052797 bismuth Inorganic materials 0.000 description 1
- 239000002639 bone cement Substances 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- GWXLDORMOJMVQZ-UHFFFAOYSA-N cerium Chemical compound [Ce] GWXLDORMOJMVQZ-UHFFFAOYSA-N 0.000 description 1
- 229910052801 chlorine Inorganic materials 0.000 description 1
- 239000000460 chlorine Substances 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 239000013065 commercial product Substances 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000012790 confirmation Methods 0.000 description 1
- 210000003298 dental enamel Anatomy 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 125000000816 ethylene group Chemical group [H]C([H])([*:1])C([H])([H])[*:2] 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- FAHBNUUHRFUEAI-UHFFFAOYSA-M hydroxidooxidoaluminium Chemical compound O[Al]=O FAHBNUUHRFUEAI-UHFFFAOYSA-M 0.000 description 1
- 238000005470 impregnation Methods 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 230000002687 intercalation Effects 0.000 description 1
- 239000004816 latex Substances 0.000 description 1
- 229920000126 latex Polymers 0.000 description 1
- 238000002386 leaching Methods 0.000 description 1
- 150000002736 metal compounds Chemical class 0.000 description 1
- NFFIWVVINABMKP-UHFFFAOYSA-N methylidynetantalum Chemical compound [Ta]#C NFFIWVVINABMKP-UHFFFAOYSA-N 0.000 description 1
- 239000000178 monomer Substances 0.000 description 1
- 229910017604 nitric acid Inorganic materials 0.000 description 1
- 229910052755 nonmetal Inorganic materials 0.000 description 1
- 235000012149 noodles Nutrition 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- RVTZCBVAJQQJTK-UHFFFAOYSA-N oxygen(2-);zirconium(4+) Chemical compound [O-2].[O-2].[Zr+4] RVTZCBVAJQQJTK-UHFFFAOYSA-N 0.000 description 1
- 239000004033 plastic Substances 0.000 description 1
- 229920003023 plastic Polymers 0.000 description 1
- 238000007494 plate polishing Methods 0.000 description 1
- -1 polyethylene Polymers 0.000 description 1
- 229920000573 polyethylene Polymers 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 229910052707 ruthenium Inorganic materials 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000010186 staining Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 239000004575 stone Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 229910003468 tantalcarbide Inorganic materials 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
- 238000004506 ultrasonic cleaning Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 208000008918 voyeurism Diseases 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
- C22B21/00—Obtaining aluminium
- C22B21/06—Obtaining aluminium refining
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
- C22B21/00—Obtaining aluminium
- C22B21/06—Obtaining aluminium refining
- C22B21/066—Treatment of circulating aluminium, e.g. by filtration
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B2003/001—Aluminium or its alloys
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Organic Chemistry (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Metal Rolling (AREA)
- Continuous Casting (AREA)
- Manufacture And Refinement Of Metals (AREA)
- Laminated Bodies (AREA)
Abstract
Description
201006578 六、發明說明： 【發明所屬之技術領域】 本發明係有關一種鋁合金厚板及其製造方法。 【先前技術】 —般而固’銘合金材料係被使用於基體基板、搬送裝 置、真空裝置用室等之半導體相關裝置、以及電機電子零 φ 件或其製造裝置、生活用品、機械零件等各種用途中。而 且’壓製用模具中所使用的模具原料，於量產用生產時使 用鋼鐵、鑄鋼等，惟於試作用時使用鋅合金鑄造物材料、 鋁合金鑄造物材料等。此外，近年來由於有多品種少量化 的傾向，於中少量生產用時普遍使用鋁合金之壓延材料或 鍛造材料等之展延材料。 於此等之中，鋁合金之壓延材料例如第2圖所示，自 熔解步驟101、經由鈍化步驟S600予以製造後，檢査變形 Φ 、板厚、及表面瑕疵等（例如參照日本特開2006-281381 號公報），以氯化乙烯製或聚乙烯製等之樹脂薄膜實施覆 蓋壓延表裏面之處理（例如神戶製鋼技報/Vol. 5 2 No. 2, •Sep.2002、註冊商標：亞魯拜斯（譯音）（ALHIGHCE) 、古河天公司（Furukawa-Sky Aluminum Corp.)製之註冊 商標：海布雷頓（譯音）（HIPLATE )等係爲已知）（ S101〜S900 ) » 使壓延表裏面以樹脂薄膜覆蓋所成的製品形態，由於 高精度鋁合金厚板大多被使用作爲精密機器等之零件，故 -5- 201006578 經由小尺寸•少數化的切割板銷售商（cutlength sheet wholesaler )進行交易。換言之，切割板銷售商係在精密 機器用途時實施爲形成骰子大小尺寸之小尺寸時之切割處 理，在真空室用途時爲部分經端銑刀加工處理時，非加工 部分形成裝置外裝材料。因此，以防止於該切削加工時產 生瑕疵爲目的時，係以高精度鋁合金厚板之壓延表裏面以 樹脂薄膜覆蓋的製品形態流通。 該鋁合金之壓延材料，通常藉由使鑄塊進行熱間壓硏 至所定厚度爲止，予以製造。然而，由於該鋁合金熱間壓 延板之板厚及平坦度，僅藉由壓延輥控制，不易得到良好 的板厚精度及平坦性（特別是壓延方向之平坦度）。而且 ’由於熱間壓延時在壓延面上會形成厚的氧化皮膜，不易 控制相同的平坦度。因此，揭示於熱間壓延後，在不會囤 積變形的程度下，以壓下率爲5%以下實施冷間壓延處理， 以提高板厚之精度的技術（例如參照專利文獻1)。 [專利文獻1]日本特開2006-316332號公報（段落〇〇27 〜0028 ) 【發明內容】 然而，前述專利文獻1之習知技術，係鋁合金材料爲 板厚約1mm之薄板者。 而且，前述之表面瑕疵，不僅爲損害製品外觀美麗之 要因外，且形成損害製品功能之重大的品質缺陷，降低製 品之處理性、同時爲除去該缺陷時必須耗費很多的工數， -6- 201006578 成爲阻害生產性的要因。例如使用骰子大小尺寸之顧客， 必須使購入製品進行加工，納入製品後，在納入製品前、 剝離被覆樹脂薄膜的階段發現瑕疵，導致失去販賣給最後 顧客的機會，或於真空室用途中，微細瑕疵爲鑄造巣時會 形成功能缺陷，惟瑕疵微細時，與損傷瑕疵沒有區別，於 判斷瑕疵的要因時極爲耗時，因此會失去販賣給最終顧客 的機會之問題。 Φ 另外，形成問題之瑕疵水準，近年來要求水準逐漸增 高，深度爲8μιη以上、圓相當直徑約爲O.lmm大小的瑕庇 ，由於可以目視發覺，會形成問題。另外，習知的製造方 法，前述水準欲使完全沒有瑕疵時會有問題。而且，主要 於真空室用途時，幾乎完全沒有直接使用原料表面，爲提 高耐腐蝕性、耐候性時，實施有耐酸鋁處理或電鍍處理。 近年來，不受原板沒有缺陷之拘束下，實施前述之表面處 理後，在下述Ti-B之溶解殘留爲原因，在壓延平行方向產 • 生約3 μπι長度之黑色線條狀的表面缺陷問題，故改善該問 題亦爲急務之一。爲對應此等表面缺陷之顧客要求時，企 求於樹脂被覆前可確實地排除該水準之表面缺陷、或藉由 表面處理所產生的表面缺陷之高精度鋁合金厚板。 本發明係有鑑於上述問題者，以提供一種可製作如真 空裝置用室之半導體相關裝置等之具有良好的板厚精度及 平坦性、且可控制因瑕疵或黑色線條等之表面缺陷的鋁合 金厚板及其製造方法爲目的。 爲解決前述課題時，本發明之鋁合金厚板，係爲使鋁 201006578 合金熱間壓延板之表面予以平滑化所形成的鋁合金厚板， 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。 如此藉由進行（樹脂薄膜被覆前之）表面平滑化，使 表面之平坦度及板厚之不均勻性限定於所定範圍，在沒有 實施冷間壓延等之薄度化加工處理下，可形成半導體相關 裝置等、被要求形狀高精度的製品時之鋁合金材料。另外 ，亦可期待具有抑制因瑕疵或黑色線條等之表面缺陷。 @ 較佳者係前述之銘合金厚板，由含有Mg: 1.5〜12.0 質量％、及含有1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、Mn : 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的鋁合金所形成 〇 藉由含有所定範圍之濃度的該元素，可形成除板厚精 度及平坦性外，強度等特性亦優異的Al-Mg系合金厚板。 0 此外，除抑制因瑕疵或黑色線條等之表面缺陷外，亦可抑 制表面之色斑（color irregularity)產生。 較佳者係前述之鋁合金厚板，由含有Μη: 0.3〜1.6質 量％、及含有1種以上之S i : 〇 . 7質量％以下、F e : 0.8質量％ 以下、Cu : 0.5質量％以下、Mn : 1 .5質量％以下、Cr : 0.3 質量％以下、Ζ η : 0.4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成的鋁合金所形成。 藉由含有所定範圍之濃度的該元素’可形成除板厚精 -8- 201006578 度及平坦性外，強度等特性亦優異的Al-Mn系合金厚板。 此外，除抑制因瑕疵或黑色線條等之表面缺陷外，亦可抑 制表面之色斑產生。 較佳者係前述之鋁合金厚板，由含有Mg : 0.3〜1.5質 量％、Si: 0.2〜1.6質量％、及含有1種以上之Fe: 0.8質量 %以下、Cu : 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％以下、Ti : 0_1質量％以下， φ 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 〇 藉由含有所定範圍之濃度的該元素，可形成除板厚精 度及平坦性外，強度等特性亦優異的Al-Mg-Si系合金厚板 。此外，除抑制因瑕疵或黑色線條等之表面缺陷外，亦可 抑制表面之色斑產生。 較佳者係前述之鋁合金厚板，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Si: 0.7質量 φ %以下、Fe : 0.8質量％以下、Cu : 3.0質量％以下、Μη : 0 · 8質量％以下、C r : 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。 藉由含有所定範圍之濃度的該元素，可形成除板厚精 度及平坦性外，強度等特性亦優異的Al-Zn-Mg系合金厚板 。此外，除抑制因瑕疵或黑色線條等之表面缺陷外，亦可 抑制表面之色斑產生。 另外，本發明之鋁合金厚板之製造方法，其係爲申請 -9- 201006578 專利範圍第1項之鋁合金厚板的製造方法，其特徵爲進行 使鋁合金溶解、形成鋁合金熔湯之溶解步驟，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。 藉由在熱間壓延板之表面上以所定的除去厚度實施平 滑化處理，可提高除板厚精度及平坦性。此外，除抑制因 瑕疵或黑色線條等之表面缺陷外，亦可抑制表面之色斑產 生。 較佳者係前述之鋁合金厚板的製造方法，其中於前述 之熱間壓延步驟前，藉由使前述鑄塊在400 °C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。 如此藉由於熱間壓延前，在鑄塊上實施熱處理，可使 鑄塊之組織予以微細化、均質化。 較佳者係前述之鋁合金厚板的製造方法，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 以鈍化的鈍化步驟。 如此藉由於熱間壓延板上實施鈍化處理，可提高熱間 -10- 201006578 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。 Φ [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。 藉由本發明之鋁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），表面之平坦度在每之壓延 -11 - 201006578 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15〜 200mm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0.2 mm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 0.2mm/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- 201006578 量爲0.2ml以下較佳，以0.1ml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 φ 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 ’自禱造即之錦合金溶湯除去氨氣。 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 O Standard ) Α06- 1993 )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系合金中任何一種，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- 201006578 [Al-Mg系合金之組成] 本發明之Al-Mg系合金、即以5 000系A1合金爲基準之 銘合金，由含有Mg: 1.5〜12.0質量％、及含有1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。 (Mg : 1·5 〜12.0質量 ％ )201006578 VI. Description of the Invention: [Technical Field of the Invention] The present invention relates to an aluminum alloy thick plate and a method of manufacturing the same. [Prior Art] The general-purpose alloy material is used in semiconductor-related devices such as a substrate, a transfer device, and a vacuum device, and a motor electronic component or its manufacturing device, household articles, and mechanical parts. In use. Further, in the production of the mold used in the mold for pressing, steel or cast steel is used for mass production, and a zinc alloy cast material or an aluminum alloy cast material is used for the test. In addition, in recent years, there has been a tendency to reduce the amount of a plurality of varieties, and a rolled material such as a rolled material of an aluminum alloy or a forged material is generally used in a small amount of production. In this case, for example, as shown in FIG. 2, the rolled material of the aluminum alloy is subjected to the passivation step 101 and the passivation step S600, and then the deformation Φ, the thickness, the surface flaw, and the like are examined (for example, refer to JP-A-2006- In the case of a resin film such as chlorinated ethylene or polyethylene, it is processed in a covered calendering table (for example, Kobe Steel Technical Report / Vol. 5 2 No. 2, • Sep. 2002, registered trademark: Yalu) ALHIGHCE, registered trademark of Furukawa-Sky Aluminum Corp.: HIPLATE is known (S101~S900) » Make the calender inside In the form of a product covered with a resin film, since high-precision aluminum alloy thick plates are often used as parts for precision machines, etc., -5-201006578 is traded through a small-size, small-sized cut-length sheet wholesaler. . In other words, the cutting board seller performs the cutting process for forming a small size of the size of the dice in the case of precision machine use, and the part of the end-milling processing when the vacuum chamber is used, the non-machined portion forms the exterior material of the device. Therefore, in order to prevent the occurrence of defects during the cutting process, the inside of the calendering table of the high-precision aluminum alloy thick plate is circulated in the form of a product covered with a resin film. The rolled material of the aluminum alloy is usually produced by subjecting the ingot to a predetermined thickness by heat. However, due to the thickness and flatness of the aluminum alloy hot-rolling sheet, it is difficult to obtain good sheet thickness accuracy and flatness (especially flatness in the rolling direction) by the calender roll control. Moreover, it is difficult to control the same flatness because a thick oxide film is formed on the calendering surface due to the thermal interval delay. Therefore, a technique in which the inter-column rolling treatment is performed at a reduction ratio of 5% or less to improve the thickness of the sheet thickness after the hot-rolling is not disclosed (for example, see Patent Document 1). [Patent Document 1] Japanese Laid-Open Patent Publication No. 2006-316332 (paragraph 〇〇27 to 0028). SUMMARY OF THE INVENTION However, the conventional technique of Patent Document 1 is a sheet material having a thickness of about 1 mm. Moreover, the aforementioned surface flaws not only damage the appearance of the appearance of the product, but also form a significant quality defect that impairs the function of the product, reduce the rationality of the product, and at the same time, must take a lot of work to remove the defect, -6- 201006578 Become a cause of hindrance to productivity. For example, customers who use the size of the tweezers must process the purchased products. After the products are incorporated, the defects are discovered before the product is introduced and the resin film is peeled off, resulting in the loss of the opportunity to sell to the last customer, or in the vacuum chamber application. When it is cast, it will form a functional defect. However, when it is fine, it is not different from the damage. It is extremely time-consuming to judge the cause of the flaw, so it will lose the opportunity to sell to the final customer. Φ In addition, the level of problem is formed. In recent years, the level of demand has been gradually increased. The depth is 8 μmη or more, and the circle is about 0.1 mm in diameter. It can be visually detected and will cause problems. In addition, the conventional manufacturing method has a problem in that the above-mentioned level is intended to be completely flawless. Further, when it is mainly used in a vacuum chamber, the raw material surface is hardly used at all, and in order to improve corrosion resistance and weather resistance, an alumite treatment or a plating treatment is performed. In recent years, under the constraint that the original sheet is free from defects, the surface treatment of the following Ti-B is carried out after the surface treatment described above, and a black line-like surface defect of about 3 μm in length is produced in the parallel direction of the rolling, Therefore, improving the problem is also one of the urgent tasks. In order to meet the customer's requirements for such surface defects, high-precision aluminum alloy slabs which are capable of reliably eliminating surface defects of the level or surface defects caused by surface treatment before resin coating are required. The present invention has been made in view of the above problems, and provides an aluminum alloy which can produce a film thickness-related precision and flatness, such as a semiconductor-related device such as a vacuum device, and can control surface defects such as defects or black lines. The thick plate and its manufacturing method are for the purpose. In order to solve the above problems, the aluminum alloy thick plate of the present invention is an aluminum alloy thick plate formed by smoothing the surface of the aluminum 201006578 alloy hot rolled sheet, and the flatness of the surface is in the rolling direction per lm. Below .2 mm, the unevenness of the sheet thickness is within ±0.5% of the desired sheet thickness. By smoothing the surface (before the resin film is coated), the flatness of the surface and the unevenness of the thickness of the surface are limited to a predetermined range, and the semiconductor can be formed without performing a thinning process such as cold rolling. An aluminum alloy material such as a related device that is required to have a high-precision shape. In addition, it is also expected to have surface defects such as suppression of defects or black lines. @ The preferred alloy thick plate is composed of Mg: 1.5 to 12.0% by mass, and one or more kinds of Si: 0.7% by mass or less, Fe: 0.8% by mass or less, and Cu: 0.6% by mass or less, Mn. : 1.0% by mass or less, Cr: 0.5% by mass or less, Zn: 0.4% by mass or less, Ti: 0.1% by mass or less, and the aluminum alloy formed by the residual component A1 and unavoidable impurities is contained. The element having a concentration in a predetermined range can form an Al-Mg-based alloy thick plate having excellent properties such as strength and flatness in addition to plate thickness precision and flatness. 0 In addition to suppressing surface defects such as flaws or black lines, it is also possible to suppress the occurrence of color irregularity. Preferably, the aluminum alloy thick plate contains Μη: 0.3 to 1.6% by mass, and one or more kinds of S i : 〇. 7 mass% or less, F e : 0.8 mass% or less, and Cu: 0.5 mass%. In the following, Mn: 1.5 mass% or less, Cr: 0.3 mass% or less, Ζ η: 0.4 mass% or less, T i : 0 · 1 mass% or less, and aluminum having a residual component of A1 and unavoidable impurities The alloy is formed. By including the element in a predetermined concentration, an Al-Mn-based alloy thick plate having excellent properties such as strength and thickness in addition to the thickness of the plate -8-201006578 and flatness can be formed. In addition, in addition to suppressing surface defects such as flaws or black lines, it is also possible to suppress the generation of stains on the surface. Preferably, the aluminum alloy thick plate is made of Mg: 0.3 to 1.5% by mass, Si: 0.2 to 1.6% by mass, and one or more kinds of Fe: 0.8% by mass or less, Cu: 1.0% by mass or less, and Μη. : 0.6 mass% or less, Cr: 0.5 mass% or less, Zn: 0.4 mass% or less, Ti: 0_1 mass% or less, φ and a residual component of A1 and an unavoidable impurity formed by an aluminum alloy. The element having a concentration in the range can form an Al-Mg-Si alloy thick plate excellent in properties such as strength and flatness in addition to plate thickness precision and flatness. In addition, in addition to suppressing surface defects such as flaws or black lines, it is also possible to suppress the generation of stains on the surface. It is preferable that the aluminum alloy thick plate contains Zn: 3.0 to 9.0% by mass, Mg: 0.4 to 4.0% by mass, and one or more kinds of Si: 0.7 mass φ% or less, and Fe: 0.8 mass% or less. Cu: 3.0 mass% or less, Μη: 0 · 8 mass% or less, C r : 0 · 5 mass% or less, Ti: 0.1 mass% or less, Zr: 0.25 mass% or less, and the residual component is A1 and unavoidable impurities The formed aluminum alloy is formed. By including the element in a predetermined concentration, an Al-Zn-Mg-based alloy thick plate having excellent properties such as strength and flatness can be formed. In addition, in addition to suppressing surface defects such as flaws or black lines, it is also possible to suppress the generation of stains on the surface. Further, the method for producing an aluminum alloy thick plate according to the present invention is the method for producing an aluminum alloy thick plate according to the first aspect of the application of the Japanese Patent Application No. -9-201006578, which is characterized in that the aluminum alloy is dissolved to form an aluminum alloy melt. a dissolving step, a dehydrogenation step of removing hydrogen from the aluminum alloy melt, a filtration step of removing the intermediate from the aluminum alloy melt from which the hydrogen is removed, and a casting of the aluminum alloy melt removing the intermediate to be manufactured The casting step of the ingot, the step of thermally pressing the ingot to a predetermined thickness, the step of rolling the inter-heat-rolling sheet, and the cutting of the inter-heat-rolled sheet to form a predetermined length and width in the rolling direction And a smoothing treatment step of smoothing the surface of the cut heat-to-heat rolled sheet, wherein in the smoothing step, the thickness of the surface of the heat-rolled rolled sheet is 2 to 5 mm per side. By performing the smoothing treatment on the surface of the inter-heat-rolled sheet at a predetermined thickness, the sheet thickness accuracy and flatness can be improved. In addition, in addition to suppressing surface defects such as defects or black lines, it is also possible to suppress the generation of color spots on the surface. Preferably, the method for producing an aluminum alloy thick plate is characterized in that the ingot is heat-treated at 400 ° C or higher and not at the melting point of the aluminum alloy for 1 hour or more before the hot-rolling step. A soaking step is performed. Thus, by heat-treating the ingot before the hot rolling, the structure of the ingot can be made finer and homogenized. Preferably, the method for producing an aluminum alloy thick plate is characterized in that a passivation step of passivating the cut heat-to-heat rolled sheet is performed before the smoothing step. Thus, by performing the passivation treatment on the inter-heat rolling plate, the characteristics of the hot plate -10-201006578 rolled plate can be improved. 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. Φ [Effect of the Invention] The thick aluminum plate of the invention is suitable for producing a semiconductor-related device requiring a correct shape because a thick plate having a desired thickness and a flat plate is formed in a thick plate having a small plastic deformation. Further, since surface defects such as flaws 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 an aluminum alloy thick 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. [Configuration 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 in the direction of each rolling -11 - 201006578 The length 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 plate thickness of 15 to 200 mm, which is not particularly limited, and may be appropriately changed depending on the use of the aluminum alloy plate thickness. Hereinafter, each element constituting the aluminum alloy thick plate of the present invention will be described. (Flatness of surface: length of 0.2 mm or less in the direction of rolling 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 201006578 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 there is such a defect in the internal member of the vacuum chamber, when the pressure is reduced in a high vacuum, the degree of vacuum can be lowered by placing the gas atoms solidified on the member on 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 slab, the ammonia gas is removed from the eucalyptus alloy in the dehydrogenation step in the following production method. The hydrogen concentration of the ingot, for example, can be cut from the ingot (before the soaking treatment). After ultrasonic cleaning with alcohol and acetone, the thermal conductivity method (LIS (Light-Metal Indusrial O Standard) is dissolved by inert gas flow. ) Α 06- 1993) 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, and is 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 material that is suitable for its purpose. Each of the elements of the aluminum alloy constituting the aluminum alloy thick plate of the present invention will be described below. -13-201006578 [Composition of Al-Mg-based alloy] The alloy of the Al-Mg-based alloy of the present invention, which is based on the 5,000-series A1 alloy, contains Mg: 1.5 to 12.0% by mass, and contains one or more kinds. 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. (Mg: 1·5 to 12.0% by 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 金因 的。 大斑 粗色 生生 產產 易易 容容 塊觀 鑄外 在面 , 表 。 時後下 %理以 量處% 質鋁量 0.7酸7W 於耐0. 大於爲 量，量 含物含 S 合之 。化S1 物間， 合屬此 201006578 (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 cause Al-(Fe)-(Mn)-Si-based intermetallic metal. Large spot, coarse color, raw production, easy to tolerate, block view, cast outside, table. After the time, the amount of the amount of aluminum is 0.7%, 7W is more than 0. It is greater than the amount, and the content contains S. Between S1, this is the same as 201006578 (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 φ 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. Further, an Al-Fe-(Mn)-(Si)-based intermetallic compound is produced by bonding to Mn and Si at the time of casting or the like. When the Fe content is more than 0.8% by mass, coarse intermetallic compounds are likely to be formed in the ingot, and the surface appearance is likely to cause stains after the alumite treatment. Therefore, the content of Fe is 0.8 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。 ❿ (Μη : 1.0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1.0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1.0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. ❿ (Μη : 1.0% by mass or less) Μ 系 has an effect of solid-melting in an aluminum alloy to improve strength. Further, when the content of Μη is more than 1.0% 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 1.0% by 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- 201006578 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。 (Ζιι : 0.4質量°/。以下）The precipitation of Cr as a fine compound at the time of casting or heat treatment has an effect of suppressing the growth of crystal grains. When the content of Cr is more than 0.5% by mass, the coarse Al_Cr-based intermetallic compound is produced as a primary crystal, and the appearance of the surface is likely to cause stains after the alumite treatment. Therefore, the content of Cr is 0.5% by mass or less. (Ζιι : 0.4 mass ° /. below)
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_ Mn系合金、即以3000系A1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 : 〇.7質量％以下 、Fe: 0.8質量％以下、Cu: 〇_5質量。/。以下、Mg: 1.5質量 %以下、Cr : 〇.3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。 (Μη: 0.3 〜1.6 質量 ％ ) 201006578 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） φ 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Α1_ 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 : 0.8質量％以下、Cu : 0.5質量％ 以下、Cr : 0.3質量％以下、Zn : 0.4質量％以下、Ti : 0 · 1 質量％以下） φ 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Al-Mg-Si系合金之各要素。本發明之 Al-Mg-Si系合金、即以6000系A1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 : 0.8質量％以下、C u : 1 · 0質量％以下、 Μ η : 0.6質量％以下、C r : 0 _ 5質量％以下、z n : 0 ·4質量°/〇 -17- 201006578 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 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_Mn-based alloy of the present invention, that is, the aluminum alloy based on the 3000-series A1 alloy, contains Μη: 0.3 to 1.6% by mass, and contains one or more kinds of Si: 〇.7% by mass or less, and Fe: 0.8% by mass. Below, Cu: 〇_5 mass. /. Hereinafter, Mg: 1.5 mass% or less, Cr: 〇.3 mass% or less, Zn: 0.4 mass% or less, and Ti: 0.1 mass% or less, and the residual component is A1 and unavoidable impurities. (Μη: 0.3 to 1.6% by mass) 201006578 Μη is solid-melted in an aluminum alloy. 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, a coarse Al·(Fe)-Mn-(Si)-based intermetallic compound is produced in the ingot, and the alumite is formed. 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) The φ Mg system has an effect of improving the strength of the aluminum alloy. When the content of Mg is 1.5% by mass, the strength when using a thick plate of Α1_ Μη alloy is sufficiently ensured, and even if 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% by mass or less, Fe: 0.8% by mass or less, Cu: 0.5% by mass or less, Cr: 0.3% by mass or less, Zn: 0.4% by mass or less, and Ti: 0 · 1% by mass or less) φ Si 'Fe, The effects of 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 Al-Mg-Si alloy will be described. The Al-Mg-Si alloy of the present invention, that is, the aluminum alloy based on the 6000 series A1 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: 0.8% by mass or less, C u : 1 · 0 mass% or less, Μ η : 0.6 mass% or less, C r : 0 _ 5 mass% or less, zn : 0 · 4 mass ° / 〇-17 - 201006578 or less, Ti: 0.1 mass% or less, and the residual component is A1 and an unavoidable impurity. (Mg: 0.3 to 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Mg2Si，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ANMg系（ 5000系A1)合金之特性。因此’ Mg之含量 爲0 · 3〜1 · 5質量％。 (S i : 0 · 2 〜1.6 質量 ％ )The effect of Mg is to increase the strength of the aluminum alloy, and the addition of Mg2Si by coexistence with Si enhances the strength of the aluminum alloy. 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 ANMg-based (5000-based A1) alloy are formed. Therefore, the content of 'Mg is 0 · 3 to 1 · 5 mass%. (S i : 0 · 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，Si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％。 (C u : 1.0質量％以下）The Si system has an effect of increasing the strength of the aluminum alloy, and when Mg is coexisted with Mg, the formation of Mg2Si' increases 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% by mass, a coarse intermetallic compound is produced in the Al-Mg-Si-based alloy. The surface appearance is likely to cause stains after the alumite treatment. Therefore, the content of Si is from 0.2 to 1.6% by mass. (C u : 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1.0質量％以下。 (Zn : 0.4質量％以下） 201006578Cu is solid-melted in an aluminum alloy and has an effect of improving strength. Further, the content of Cu is more than 1.0 mass%. At the time, the corrosion resistance of the Al-Mg-Si alloy is lowered. Therefore, the Cu content is 1.0% by mass or less. (Zn: 0.4% by mass or less) 201006578
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 : 〇.6質量％以下、Cr : 0.5質量 %以下、Ti : 〇.1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: 〇.6 mass% or less, Cr: 0.5 mass% or less, and Ti: 〇.1 mass% or less)
Fe、Mn、Cr、Ti之各效果，由於與Al-Mg系合金者相 φ 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 AhAn-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Si : 0.7質量％以下、Fe : 0.8質量％以下、Cu : 3.0質量％以下、Μη : 〇.8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 aluminum alloy based on the 7000 series A1 alloy of the AhAn-Mg alloy of the present invention contains Zn: 3.0 to 9.0% by mass, Mg: 0.4 to 4.0% by mass, and one or more Si: 0.7 masses. % or less, Fe: 0.8 mass% or less, Cu: 3.0 mass% or less, Μη: 〇.8 mass% or less 'Cr: 0.5 mass% or less ・, Ti: 0.1 mass% or less, Zr: 0.25 mass% or less, and residual The composition is formed of an aluminum alloy formed of A1 and unavoidable impurities. (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％。 -19- 201006578 (1^^: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-treated thick surface is less 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. -19- 201006578 (1^^: 0_4~4.0% by 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 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'
Mg之含量爲0.4〜4.0質量％。 (Cu : 3.0質量％以下）The content of Mg is 0.4 to 4.0% by mass. (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具有使鋁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，且耐酸鋁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: 〇_7質量°/。以下、Fe: 0.8質量％以下、Μη: 0.8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 aluminum alloy finer and more stable. Further, when the content of Zr is more than 0.25 mass%, it is easy to produce a coarse @intermetallic compound, and the surface appearance after the alumite treatment is likely to cause color spots. Therefore, the content of Zr is 0.25 mass% or less. (Si: 〇_7 mass ° /. below, Fe: 0.8% by mass or less, Μ η: 0.8% by mass or less, Cu: 0.5% by mass or less, Ti: 0.1 mass ° / or less)
Si、Fe、Mn、Cr、Ti之各效果，由於與A1_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- 201006578 金、Al-Zn-Mg系合金中之任何一種，無法避免的雜質之 V，B等之含量，各爲0.01質量％以下時，不會影響本發明鋁 合金厚板之特性。然而，以防止漿料造塊時之鑄塊破裂爲 目的時，添加由Ti與Bi之母合金所形成的微細化劑，如下 所述，粗大的Ti-B粒子溶解殘留時，在耐酸鋁處理或電鍍 處理等之表面處理後，會產生黑色線條。因此，使用Al-Ti 之微細化劑等，以沒有添加B較佳，藉由添加B，產生黑色 φ 線條，如下所述，藉由適當的平滑化處理，可除去黑色線 條。 (鋁合金厚板之製造方法） 其次，本發明之鋁合金厚板的製造方法，參照圖面予 以說明。第1圖係爲本發明之鋁合金厚板的製造方法之流 程圖。本發明之鋁合金厚板的製造方法，預先使前述任何 一種之組成的鋁合金熔解，形成鋁合金熔湯（熔解步驟 Φ S11)，自鋁合金熔湯各除去氫氣及中間物（脫氫步驟S12 、過濾步驟S13)。使該鋁合金熔湯鑄造，製造鑄塊（鑄 造步驟S14)，使鑄塊熱間壓延成所定厚度，製造熱間壓 延板（熱間壓延步驟S30)。然後，切斷熱間壓延板（切 斷步驟S50 )，使表面進行平滑化、加工處理（平滑化處 理步驟S70)。而且，於熱間壓延前，亦可使鑄塊藉由熱 處理予以均質化（均熱處理步驟S20)。此外，亦可矯正 熱間壓延板之變形（矯正步驟S40 )。另外，亦可進行熱 間壓延板鈍化處理（鈍化步驟S60)。而且，如此製造的 -21 - 201006578 鋁合金厚板，再經由檢查步驟S80、樹脂薄膜被覆步驟S 90 ，形成表裏面以樹脂薄膜被覆的製品形態。而且’第1圖 中簡單說經由樹脂薄膜被覆步驟S90予以完成’本發明之 鋁合金厚板，爲完成平滑化處理步驟s 70者。於下述中， 說明各步驟之詳細。 (熔解步驟） 熔解步驟S11，係可使所定組成之鋁合金熔解，形成 鋁合金熔湯的步驟，以習知的設備、方法進行。 (脫氫步驟） 脫氫步驟S12，係自鋁合金熔湯除去氫氣的步驟，使 鋁合金熔湯藉由熔融（fluxing)、氯精練、或線上精練等 ，適當地除去氫氣。而且，使用作爲脫氫裝置之史萊姆（ SNIFF)等之回轉式脫氫裝置或孔栓（porous plug )(參 照特開2002-146447號公報）時，可更爲適當地除去。 (過濾步驟） 過濾步驟S13，藉由過濾裝置，自鋁合金熔湯主要除 去氧化物或非金屬之中間物的步驟。過濾裝置例如設置使 用約1mm之粒子的氧化鋁之陶瓷管，藉由於其中通過鋁合 金熔湯’可除去前述之氧化物或中間物。 藉由脫氫步驟S12及過濾步驟S13，於繼後的鑄造步驟 S14中’可形成抑制內部缺陷之高品質的鋁合金鑄塊。而 -22- 201006578 且，由於可抑制氧化物之堆積物（dross)的堆 堆積物除去之作業。 (鑄造步驟） 鑄造步驟S14，例如在含有水冷鑄型所構 置，使鋁合金熔湯形成正方形形狀等之所定形 固，爲製造鋁合金鑄塊時之步驟。鑄造方法可 φ 鑄造法。半連續鑄造法係在底部經開放的金屬 型，自上方注入金屬之熔湯，且自水冷鑄型的 出經凝固的金屬，製得所定厚度之鑄塊。該半 ，亦可在縱向、橫向中任何方向進行。 (均熱處理步驟-處理溫度：未達4 0 0°C以上鋁 、處理時間：1小時以上） 均熱處理步驟S2 0，藉由在鋁合金鑄塊上 〇 ，除去內部應力，使鑄造時偏析的溶質元素予 且使鑄造時結晶的金屬間化合物予以擴散固溶 質化之步驟。熱處理藉由常法、在400 °c以上 金之熔點的溫度，保持1小時以上進行。均熱 達400°C，前述效果不充分。而且，處理時間3 金屬間化合物之固熔不充分，容易析出。另外 溫度達到本發明之鋁合金的熔點時，部分鋁合 產生稱爲熔解的燃燒（burning)之現象，容易 厚度之表面厚板的表面缺陷之原因。因此，均 積，可降低 成的鑄造裝 狀，予以凝 使用半連續 製之水冷鑄 底部連續取 連續鑄造法 合金之溶點 實施熱處理 以均質化， ，使組織均 、未達鋁合 處理溫度未 i達1小時， ，均熱處理 金塊之表面 形成鋁合金 熱處理溫度 -23- 201006578 ，爲40(TC以上、未達鋁合金之熔點，且進行1小時以上。 (熱間壓延步驟） 熱間壓延步驟S30，係爲使鋁合金鑄塊進行熱間壓延 ，形成所定厚度之板材（鋁合金熱延板）之步驟。熱間壓 延方法，可使用可逆式（可逆）熱間壓延機。使鋁合金鑄 塊昇溫至所定的溫度爲止，藉由可逆式熱間壓延機進行壓 下，製造所定厚度之鋁合金熱延板。以該步驟之板厚（鋁 _ 合金熱延板之板厚），對鋁合金厚板之企求的板厚而言爲 藉由下述之平滑化處理步驟S70加入減少成分之板厚’以 約15〜200mm較佳。 (矯正步驟） 矯正步驟S40，係爲矯正以鋁合金熱延板之熱間壓延 所產生的變形，予以平坦化的步驟，以伸縮器（stretcher )或拉伸水平器等之習知的設備、方法進行。 n (切斷步驟） 切斷步驟S50，係爲鋁合金熱延板切斷成企求的長度 (及寬度）之步驟。 (鈍化步驟） 鈍化步驟S 60，係爲藉由在鋁合金厚上實施熱處理’ 除去內部應力，且使內部組織均一化的步驟。而且’藉由 -24- 201006578 熔體化處理及時效處理實施調質處理。而且，此等處 可平滑化處理步驟S70後進行。而且，例如日本特開[ 115617公報中揭示，可藉由實施熱處理，提高表面之 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 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〜 。藉由使除去厚度爲2mm以上時，使平坦度、板厚之 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 實施耐酸鋁處理或電鍍處理等之表面處理後，朝壓延 方向產生約3μπι長度之黑色線條狀表面缺陷的缺點， 發明人等再三深入硏究該原因的結果，發現防止鑄塊 • 或鑄造時之鑄塊微細化劑（結晶粒微細化劑）之Ti-B 爲漿料造塊之鑄型附近之急冷凝固部溶解、所殘留者 此，使除去厚度爲2mm以上，即使有鑄塊微細化劑之 之溶解、殘留，亦可除去該物，故即使進行耐酸鋁處 電鍍處理，也不會有產生黑色線條狀表面缺陷的情形 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 鑽石刀（diamond bite )切削等之切削法、使表面以 等切削的硏削法、拋光（buffing)硏磨等之硏磨法等 理亦 S 63-平坦 面（ 5 mm 不均 束， 平行 惟本 破裂 ，係 。因 Ti-B 理或 。而 削或 抵石 ，惟 -25- 201006578 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、二氧化锆等之單 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#120〜#220。而 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15OOrpm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8μιη以上，於檢查時無法判斷的 瑕疵大小爲20μιη爲止，8〜20μιη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S 80 ，檢查有關變形、板厚、及表面瑕疵等後，藉由樹脂薄膜 -26- 201006578 被覆步驟S90，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 : JIS5 05 2合金、51 : JIS5 08 3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5〇〇mm 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25 mm、與厚度約 • 2 0mm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1000mm後，對壓延面（兩面）而言進行 平滑化處理，形成厚度2〇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之錫合金熱延板。 -27- 201006578 端銑刀加工處理，係改造WAS SER GmbH (德 械製造商、GmbH爲股份有限公司）之端銑刀加X 刀）使用。粗片係超硬，加工片係爲鑽石，加工代 就零點而言之圓盤的押入量，總値約爲2.5mm/單片 調整進行加工。 具體而言，圓盤下面之圓周附近裝設有30個I 個加工片，使圓盤降落於被加工物後，予以回轉， 至板長度方向進行切削加工處理。而且，由於加工 之飛出量較粗片稍微飛出下予以裝設，使粗片之切 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（ Machine Mfg. Co., Ltd)製之鋁板拋光硏磨機器在 磨輥部上可裝設硏磨不織布滾輪予以改造、使用。 使用光陽社股份有限公司（KOYO-SHA Co.，Ltd) 乳膠（POLITEX;註冊商標）KF滾輪 MA (粗目（ 、外徑φ 400mm、油含浸，砥粒種使用褐色熔融氧 黏合劑使用樹脂黏合劑）。 然後，以加工代工約爲3·0μπι/單片所形成的條 盪（2次來回））實施硏磨處理。而且，硏磨代工 驗的硏磨部之段差以Vecoo instruments Inc·製（ 之「WYKO NT3300 (表面形狀測定系統）」測定 測定凹凸之深度，予以計測確認。 (Al-Mn系合金） 國之機 機（銑 工係爲 下予以 &片、2 藉由送 處理片 削面切 Nomizu 拋光硏 滾輪係 製之聚 #150) 化鋁、 件（振 係使試 美國） 形狀， 201006578 使表1所示之合金No.3a〜3e之組成的銘合金（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500mm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 φ 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25 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。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。 鬱 • 29 - 201006578 【表1】 合金 鋁合金成分醜質量％) No. Si Fe Cu Mn Cr Zn Ti Al** 5a 2.6 0.1 0.4 - - - 0.01 残留成分 5b 2.6 0.1 0.4 - 0.3 - - 0.01 殘留成分 5c 4.4 0.1 0.4 — - - - 0.01 殘留成分 5d 7.0 D.1 0.4 - - - 0.01 挪成分 5e 10.5 0.1 0.4 - - - - 0.01 贿齡 5f 4.4 0.3 0.5 0.3 - - - 0.01 殘留成分 5k 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 細成分 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 残留成分 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 瓶成分 5m* 1.4* 0.1 0.4 - - - - 0.01 殘留成分 5n * 13.0* 0.1 0.4 - - - - 0.01 嫌留成分 5o * 4.4 0.8* 0.4 - - - - 0.01 細成分 5d * 4.4 0.1 1.0* - - - 0.01 瓶成分 5q * 4.4 0.1 0.4 0.7* - - - 0.01 棚成分 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 瓶成分 5t* 4.4 0.1 0,4 - - - 0.5* 0.01 瓶成分 5u * 4.4 0.1 0.4 - - - - 0.1铲 残留成分 5v Z6 0.1 0.4 - - - - 一 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 *:逋當範園外林:含有不可避免的雜質 [實施例1 :評估] 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- 201006578 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 ( φ 19.94〜20.06mm)之範圍者，板厚精度優異，評估爲「◎ 」，20.0±0.10mm ( 2 0 · 0mm± 0.5 %、 1 9 · 90 〜2 0 . 1 0mm )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90N/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（15%硫酸、 20°C、電流密度2A/dm2)形成厚度ΙΟμηι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 - 201006578 <耐酸鋁處理後因瑕疵之表面性質評估> 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「X」。 <耐酸鋁處理後因黑色線條之表面性質評估> 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，調査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。 <因耐鋁酸處理後之色斑之表面性質評估> 觀察前述經耐酸鋁處理的表面之外觀，外観沒有色斑 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「X」。 -32- 201006578 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。The respective effects of Si, Fe, Mn, Cr, and Ti are the same as those of the A1_Mg-based alloy, and therefore will be omitted. Further, in the Al-Mg-based alloy, the Al-Mn-based alloy, the Al-Mg-Si-bonded -20-201006578 gold, and the Al-Zn-Mg-based alloy, the unavoidable impurities V, B, etc. When the content is 0.01% by mass or less, the characteristics of the aluminum alloy thick plate of the present invention are not affected. However, in order to prevent cracking of the ingot at the time of slurry agglomeration, a refining agent formed of a mother alloy of Ti and Bi is added, and as described below, when the coarse Ti-B particles are dissolved and left, the alumite treatment is performed. After the surface treatment such as plating treatment, black lines are generated. Therefore, it is preferable to use a refiner of Al-Ti or the like without adding B, and by adding B, a black φ line is produced, and as described below, the black line can be removed by an appropriate smoothing treatment. (Manufacturing Method of Aluminum Alloy Thick Plate) Next, a method for producing the aluminum alloy thick plate of the present invention will be described with reference to the drawings. Fig. 1 is a flow chart showing a method of manufacturing an aluminum alloy thick plate of the present invention. In the method for producing an aluminum alloy thick plate according to the present invention, the aluminum alloy having any of the above composition is melted to form an aluminum alloy melt (melting step Φ S11), and hydrogen and an intermediate are removed from the aluminum alloy melt (dehydrogenation step) S12, filtering step S13). The aluminum alloy melt is cast to produce an ingot (casting step S14), and the ingot is heat-calendered to a predetermined thickness to produce a hot intercalation sheet (intercalating step S30). Then, the inter-heat rolling plate is cut (cutting step S50), and the surface is smoothed and processed (smoothing processing step S70). Further, the ingot may be homogenized by heat treatment before the heat is rolled (the soaking step S20). Further, the deformation of the inter-heat rolling plate can be corrected (correction step S40). Alternatively, the inter-heat rolling plate passivation treatment (passivation step S60) may be performed. Further, the -21 - 201006578 aluminum alloy thick plate thus produced is further formed into a product form covered with a resin film by the inspection step S80 and the resin film coating step S 90 . Further, in the first drawing, the aluminum alloy thick plate of the present invention is completed by the resin film coating step S90, and the smoothing process step s 70 is completed. The details of each step are explained below. (Melting step) The melting step S11 is a step of melting an aluminum alloy of a predetermined composition to form an aluminum alloy melt, which is carried out by a known apparatus and method. (Dehydrogenation step) The dehydrogenation step S12 is a step of removing hydrogen from the aluminum alloy melt to appropriately remove the hydrogen gas by melting, chlorine scouring, or wire scouring. Further, when a rotary dehydrogenation apparatus such as SNIFF or a porous plug such as a dehydrogenation apparatus is used (refer to Japanese Laid-Open Patent Publication No. 2002-146447), it can be more suitably removed. (Filtering step) The filtering step S13 is a step of mainly removing an oxide or a non-metal intermediate from the aluminum alloy melt by means of a filtering device. The filtering means is, for example, a ceramic tube of alumina using particles of about 1 mm, by which the aforementioned oxide or intermediate can be removed by the aluminum alloy melt. By the dehydrogenation step S12 and the filtration step S13, a high-quality aluminum alloy ingot which suppresses internal defects can be formed in the subsequent casting step S14. And -22-201006578, because of the operation of suppressing the deposition of heap deposits of oxide deposits (dross). (Casting Step) The casting step S14 is a step of producing an aluminum alloy ingot by, for example, a configuration in which a water-cooled mold is used and the aluminum alloy melt is formed into a square shape or the like. The casting method can be φ casting method. The semi-continuous casting method is an open-cast metal type at the bottom, injecting a molten metal from the top, and a solidified mold from a water-cooled mold to obtain an ingot of a predetermined thickness. The half can also be carried out in any direction in the longitudinal direction and the lateral direction. (Homogeneous heat treatment step - treatment temperature: less than 400 ° C above aluminum, treatment time: 1 hour or more) The soaking step S20, by removing the internal stress on the aluminum alloy ingot, causing segregation during casting The solute element is a step of diffusing and solidifying the intermetallic compound crystallized during casting. The heat treatment is carried out by a conventional method at a temperature of 400 ° C or more and a melting point of gold for 1 hour or more. The soaking temperature is up to 400 ° C, and the aforementioned effects are insufficient. Further, in the treatment time 3, the solid solution of the intermetallic compound is insufficient and is easily precipitated. Further, when the temperature reaches the melting point of the aluminum alloy of the present invention, part of the aluminum alloy causes a phenomenon called melting, which is a cause of surface defects of the surface thick plate which is easy to be thick. Therefore, the product can be reduced into a casting shape, and the water-cooled casting bottom of the semi-continuous system is continuously used to continuously heat the melting point of the continuous casting alloy to perform homogenization, so that the microstructure is not reached. i for 1 hour, the surface of the heat-treated gold nugget forms the heat treatment temperature of the aluminum alloy -23-201006578, which is 40 (above TC, less than the melting point of the aluminum alloy, and is carried out for more than 1 hour. (Hot-calendering step) Inter-calendering step S30 is a step of forming a plate of a predetermined thickness (aluminum alloy heat-expanding plate) by hot-rolling an aluminum alloy ingot. The inter-heat rolling method can use a reversible (reversible) hot-rolling calender. The block is heated to a predetermined temperature, and is pressed by a reversible inter-heating calender to produce a hot-decked aluminum alloy sheet having a predetermined thickness. The thickness of the sheet (the thickness of the aluminum-alloy heat-expanded sheet) is aluminum. The sheet thickness of the alloy thick plate is preferably about 15 to 200 mm by adding the thickness of the reduced component by the smoothing treatment step S70 described below. (Correction step) Correction step S40 is correction The step of flattening the deformation caused by the inter-heat rolling of the aluminum alloy heat-expanding plate is carried out by a conventional apparatus or method such as a stretcher or a stretch level. n (cutting step) cutting The step S50 is a step of cutting the aluminum alloy heat-expanding plate into a desired length (and width). (passivation step) The passivation step S 60 is performed by performing heat treatment on the aluminum alloy thickness to remove internal stress, and A step of homogenizing the internal structure. Further, the quenching and tempering treatment is carried out by the melt treatment and the aging treatment by -24 to 065, 078. Further, the smoothing treatment step S70 can be performed. Further, for example, Japanese special opening [115617] It is disclosed in the publication that the degree of surface can be increased by performing heat treatment. (Smoothing treatment step) The smoothing treatment step S70 is to smooth the surface of the aluminum alloy heat-expanding sheet φ calendering surface and adjust the thickness of the sheet. step. Here, the thickness of the surface of the heat-expanding plate is 2 to 2 on each side. When the thickness is 2 mm or more, the flatness and the thickness of the sheet are appropriately adjusted, and surface defects due to flaws can be suppressed. Further, as described above, in recent years, after the surface treatment such as the alumite treatment or the plating treatment is not performed without the defect of the original sheet, the black line-like surface defect having a length of about 3 μm is generated in the rolling direction, and the inventors have further inquired. As a result of the reason, it was found that the Ti-B which prevents the ingot from being ingot or the ingot of the ingot during casting is dissolved in the quenched solidified portion in the vicinity of the mold in which the slurry is agglomerated, and remains. When the removal thickness is 2 mm or more, even if the ingot refining agent is dissolved or left, the object can be removed. Therefore, even if the alumite plating treatment is performed, black line-like surface defects are not generated. In terms of handleability or cost, the thickness is removed to be 5 mm or less. For the smoothing method, a cutting method such as cutting a diamond bite with an end mill, a boring method such as cutting a surface, and a honing method such as buffing honing can be used. Also S 63-flat surface (5 mm uneven beam, parallel only rupture, system. Due to Ti-B rational or curved. Or cut or stone, but -25- 201006578 is not subject to these restrictions. In addition, for smoothing In the processing step S70, the surface defect is suppressed by the flatness, the unevenness of the thickness, the ridge or the black line, and the like, and then the hair line process is performed. The surface of the board is coated with a rolling target. The method of hairline processing, the belt type, or the roller type, etc. are known, and any method can be used, and the belt processing method such as belt type or roller type can be used. The honing non-woven fabric to be used is, for example, formed of a monomer such as alumina, tantalum carbide, zirconium dioxide or the like as a cerium seed, or a mixture thereof, and an adhesive such as a resin or a bone cement. The grain number is, for example, the thicker #120 of the commercial product. #220. Moreover, when using a belt type or a roller type honing non-woven fabric having an outer diameter of Φ 400 mm, since it contains oil for preventing baking, it is preferable to perform the yarn processing at a number of revolutions of 15 rpm or less, but it is not necessary. In addition, as for the surface defects caused by the flaw, the size of the flaw that can be recognized by the human eye is 8 μm or more, and the size of the crucible that cannot be judged at the time of inspection is 20 μm, and the depth of 8 to 20 μm is by the foreign matter. Or the roll is produced by the push, and the defect is not a defect of the original function. Therefore, since the push-in can be processed by the hairline processing (processing: about 2 to 3 μm), the smooth portion of the surface of the thick plate is Since the boundary is formed in a smooth state, the effect of the functional defect can be easily determined. Further, when the economy is not used, even if only the hairline processing is performed, the effect of the present invention can be obtained if the surface is cut by 2 mm or more. The manufactured aluminum alloy slab is further inspected by the inspection step S80 after the deformation, the thickness, the surface flaw, etc., by the resin thin -26-201006578 Coating step S90, the inside of the watch is covered with a resin film. [Embodiment] In the above, the best mode for carrying out the invention will be described, and in the following, the embodiment of the effect of the present invention is confirmed. The present invention is not limited to the comparative examples which satisfy the requirements of the present invention. Further, the present invention is not limited to the examples. [Example 1: Preparation of test materials] (Al-Mg alloy) The alloys of the alloy No. 5a to 5v (5k: JIS5 05 2 alloy, 51: JIS5 08 3 alloy, 5v without Ti or B added) are dissolved, dehydrogenated, filtered, and cast to obtain a plate thickness. 5 〇〇 mm ingot. 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 length of 2000 mm x a width of 1000 mm, the rolled surface (both sides) was smoothed to form an aluminum alloy thick plate (cutting plate) having a thickness of 2 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. Further, the end mill cutter processing is performed using an aluminum alloy heat-expanding plate having a thickness of about 25 mm, and only a hairline processing processor is used to use a tin alloy heat-expanding plate having a thickness of about 20 m. -27- 201006578 The end mill processing is used to transform the end mill and X knife of WAS SER GmbH (German manufacturer, GmbH). The slab is super-hard, and the processed piece is made of diamond. The processing is performed on the zero point of the disc. The total 値 is about 2.5mm / single piece adjustment for processing. Specifically, 30 pieces of one processed piece are placed near the circumference of the lower surface of the disk, and the disk is returned to the workpiece, and then rotated to perform the cutting process in the longitudinal direction of the plate. Further, since the amount of flying out of the processing is slightly smaller than that of the thick piece, the cutting piece is cut into the subsequent processed piece, and the cutting is continued. The processing of the hairline is to make the aluminum plate polishing and honing machine manufactured by Machine Mfg. Co., Ltd., which can be modified and used by honing non-woven rollers on the grinding roller. Use KOYO-SHA Co., Ltd. Latex (POLITEX; registered trademark) KF roller MA (thickness (outer diameter φ 400mm, oil impregnation, use of brown melt oxygen adhesive for resin type) Then, the honing treatment is carried out by a processing (about 2 times back and forth) formed by a processing foundry of about 3.0 μm/monolith. In addition, the depth of the unevenness measured by the "WYKO NT3300 (Surface Shape Measurement System)" manufactured by Vecoo Instruments Inc. ("WYKO NT3300 (Surface Shape Measurement System)") was measured and confirmed. (Al-Mn alloy) Machine (Milling machine is the next & film, 2 by processing the sliced noodle cut Nomizu polished 硏 roller system made of poly #150) aluminum, pieces (vibration makes the test US) shape, 201006578 as shown in Table 1 The alloy of the alloy No. 3a to 3e (3e: Ti, B is not added) is dissolved, dehydrogenated, filtered, and cast to produce an ingot having a thickness of 500 mm. By calendering, an aluminum alloy heat-expanding plate having a thickness of about 25 mm and a thickness of about 20 mm is produced. After the aluminum alloy heat-expanded plate is cut into a rolling direction length of 2000 mm×width of 1 000 mm, the rolling surface (both sides) is smoothed. An aluminum alloy thick plate (cutting plate) with a thickness of 20 mm is formed. Moreover, when Ti is contained as φ to prevent cracking of the ingot, a Ti-B master alloy is added. The smoothing process is performed by end milling and end milling. Knife processing + hairline processing ( Three methods, such as belt honing and non-woven fabrics, and hairline processing, are used to compare the effects. Moreover, the end mill cutter is used to heat the aluminum alloy sheet with a thickness of about 25 mm, and only the hairline processing is performed. For the processor, an aluminum alloy heat-expanding plate having a thickness of about 20 m is used. In addition, the method of processing the end mill and the hairline processing is the same as that of the Al-Mg alloy described above. 郁• 29 - 201006578 [Table 1] Alloy 5% mass of aluminum alloy composition) No. Si Fe Cu Mn Cr Zn Ti Al** 5a 2.6 0.1 0.4 - - - 0.01 Residual component 5b 2.6 0.1 0.4 - 0.3 - - 0.01 Residual component 5c 4.4 0.1 0.4 — - - - 0.01 Residue Ingredient 5d 7.0 D.1 0.4 - - - 0.01 Fraction 5e 10.5 0.1 0.4 - - - - 0.01 Bribe age 5f 4.4 0.3 0.5 0.3 - - - 0.01 Residual component 5k 4.4 0.1 0.3 - 0.05 - - 0.01 Residual component 5h 4.4 0.1 0.3 - - 0.05 - 0.01 Fine 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 bottle Ingredients 5m* 1.4* 0.1 0.4 - - - - 0.01 Residual Residue 5n * 13.0* 0.1 0.4 - - - - 0.01 Suspected ingredient 5o * 4.4 0.8* 0.4 - - - - 0.01 Fine component 5d * 4.4 0.1 1.0* - - - 0.01 Bottle component 5q * 4.4 0.1 0.4 0.7* - - - 0.01 Shelf composition 5r * 4.4 0.1 0.4 - 1.1 * - - 0.01 Residual component 5s * 4.4 0.1 0.4 - - 0,6* - 0.01 Bottle composition 5t* 4.4 0.1 0,4 - - - 0.5* 0.01 Bottle composition 5u * 4.4 0.1 0.4 - - - - 0.1 Shovel residual component 5v Z6 0.1 0.4 - - - - One 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 *: 逋当范园外林: contains unavoidable impurities [Example 1: Evaluation 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 curling amount of -30-201006578 (flatness) of 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 (φ 19.94~20.06mm), and the plate thickness is excellent. The evaluation is “◎”, 20.0±0.10mm (2 0 · 0mm± 0.5 %, 1 9 · The range of 90 ~ 2 0 . 1 0mm ) is better, and the evaluation 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. the above. (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 ΙΟμηι was formed on the surface of the test material by an alumite treatment of sulfuric acid (15% sulfuric acid, 20 ° C, current density 2 A/dm 2 ). Then, observe the surface properties of the surface defects and the surface properties of the black lines - 31 - 201006578 <Evaluation of the surface properties of the alum after treatment with an acid-resistant aluminum> Observe the appearance of the aluminate-treated surface, 40 sheets are judged by the naked eye In the cutting plate, when there is no one due to the surface properties of the crucible, it is excellent as "◎", and 40 pieces of the cutting plate judged by the naked eye have 1 to 4 sheets due to the surface properties of the crucible. "〇", when 40 sheets of the cut sheets judged by the naked eye were evaluated for the surface properties of the crucible, it was "X". <Evaluation of surface properties of black lines after alumite treatment> Observing the black lines of the alumite-treated surface (with no functional defects), visually observing the absence of black lines by the naked eye, and evaluating the surface properties by black lines "◎", the person who has black lines is observed with the naked eye, and the "X" is evaluated by the black line. 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. <Evaluation of surface properties of stains after resistance to aluminic acid treatment> Observing the appearance of the above-mentioned surface treated with an alumite treatment, the appearance of the surface of the stain is not good, and it is evaluated as "〇", colored The spotted person was evaluated as "X" because of the poor surface properties of the stain. -32- 201006578 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】 齡 藉由JS«W3加工之平滑ft*理 藉由齡刀加工平理 No> 平酿 (mm/m) «Β 彍度(N/mml) 理後 耐雜處理後 | 精度 拉伸鄉 酣力 挪痲之 表面賊 mk^mm 之表面賊 表面賊 Cmm/m) 嫌度 @3@疵之 表面战 因黑触條 之表面賊 因 表面蚀 0.15 217 102 〇 〇 0.14 〇 〇 0.15 ψ 228 110 〇 〇 0.15 d 〇 〇 Em 0.T6 294 143 ◎ 〇 〇 0.16 Θ 〇 〇 0.1ft '331 170 〇 〇 0.17 & 〇 〇 ΓΜ Q.19 © 385 186 © 〇 〇 0.18 〇 〇 EH 0.1β 309 139 Θ 〇 〇 0.18 & 〇 〇 Em 0.16 305 146 Θ 〇 〇 0.16 Θ 〇 〇 EM 0.16 314 145 Θ 〇 〇 0.15 〇 〇 〇 0.17 ❺ 318 155 Θ 〇 〇 0.17 ❺ 〇 〇 ES 0.18 305 144 @ 〇 〇 0.18 © 〇 〇 wm aie 222 108 〇 〇 0.15 〇 〇 E· 0.1β © 307 145 〇 〇 0.18 〇 〇 0.15 171 69 〇 〇 〇 0.15 © 〇 〇 一 — - - — — — — — 0.17 322 160 〇 X 0.17 〇 X EX 0.17 Ο 306 150 Θ 〇 X 0.16 〇 X 0.18 〇 320 163 ύ 〇 〇 0.18 〇 〇 ΕΏ an €) 324 162 & 〇 X 0.17 ❹ 〇 X 0.18 322 158 0 〇 X 0,17 〇 X Eia 0.17 €> 305 146 θ 〇 〇 0.17 ❺ 〇 〇 0.18 €> 310 147 〇 〇 〇 0.18 〇 〇 EM 0.1$ 215 101 ο 〇 〇 0.14 ❽ 〇 〇 E9I wm 0.1$ ◎ 94 38 〇 〇 0.15 〇 〇 0.16 ρ 103 41 〇 〇 0.15 & 〇 〇 EBC 0.16 84 37 ❽ 〇 〇 0.16 〇 〇 gyc 0.17 117 49 〇 X 0.16 d 〇 X wm 0.1$ €> 92 37 〇 〇 0.H 〇 〇 適««外 -33- 201006578 【ε揪】 耐麟處理後 因色斑之 表面性質 〇 ο 0 o 〇 o o o o o o o 0 I X X o X X ο 0 0 0 ο ο X Ο 1黯馥 X X X X X X X X X X X X X I X X X X X X X ο X X X X Ο 鋁合金熱延板 1111 X X X X X X X X X X X X X I X X X X X X X X X X X X X 強度(N/mm2) 耐力 g S s s 'Si CM in 5? csl CM in «Μ 〇 I <D CO 卜 CO s 5i 萃 5 3 LO ιη C0 ιη «ο ιτ> ιη 拉伸強度 eg CVI CSJ 筘 c〇 辑 00 Oi eg Oi CM 袋 R 丨 297__I Oi o 另 in I CM o a> CM «μ m evi 异 1 28β 2 CNJ τ» 〇2 00 <0 β> CM ί 精度 ◎ © o o o ◎ 〇 o o 〇 ◎ o ◎ I © o ο ◎ ο ο Ο ◎ © ο ◎ ο ◎ 平坦度 (mm/m) 0.41 1 I 0 *2 I 0.50 I I 0.62 I 0.69 I 0.47 I I 048 | I 0 47 I 0.50 0.48 I 0.43 I I 0.49 I I 0.42 I I 1 0.48 1 1 0.50 1 0.49 1 〇·*8 1 0.48 1 0.50 1 1 0.50 1 0.40 1 0.41 I 0.42 I 0.41 I 0.44 I 0.41 銘合金_ 藉由髮線加工之平滑化處理 耐酸銘處理後 因色斑之 表面性質 ο ο o o O o o o o o 〇 〇 o I X X ο X X ο ο ο ο ο ο X ο 雄IK 翡 E-N X X X X X X X X X X X X X I X X X X X X X ο X X X X ο SI ο 0 o o o o o 〇 o 0 o o o I 〇 o ο Ο ο ο ο 0 ο ο ο ο ο S 精度 ◎ ◎ o o o ◎ 0 o o 0 © o ◎ 1 © o ο ◎ 0 ο ο ◎ ◎ ο ◎ ο ◎ 平坦度 (mm/m) 0-41 I I 0-4t | I 0.50」 0.61 I I 0.68 I I 047 | 丨 0-48 I I 0-47 I I 0.49 I I 0-48 i I 0.43 I 0-48 | I 0.42 | 1 1 0 48 1 1 0.50 1 0.48 ! 1 0.48 1 1 0.47 1 1 0.50 1 I 0.49 1 1 0.40 1 0.41 I 0.41 1 0.41 ]0.43 1 0.41 合金 6 5 ΙΛ 5 ίο in i5 in' ίο ΰ5 I 5fTVK 5n * 5o *1 * in * 5r* 5s* 5t* 1 5u * 1Π <s I 3c * 3d * -34- 201006578 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. 5 m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No.5n所形成的鋁合金厚板，由於Mg含量 φ 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 Φ 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- 201006578 ，由於除去量適當，確認可防止黑色線條產生。而且，由 5v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。 由合金No.3a、3b、3e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.3c 所形成的鋁合金厚板，由於Μη之含量不足，無法得到充分 的強度。另外，由合金No. 3d所形成的鋁合金厚板，由於 Μη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 +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 -36- 201006578 ，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 φ 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之組成的銘合金溶解，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20mm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- 201006578 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 25 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A1-Mg系合金時相同。此外，使所 得的鋁合金厚板在520°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）[Table 2] Age by JS «W3 processing smooth ft * by the age of the knife processing leveling No > flat brewing (mm / m) « Β 彍 degree (N / mml) after the treatment of miscellaneous treatment | precision pull伸 酣 挪 挪 挪 挪 m m m m m m m m m m m m m @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ @ 228 110 〇〇0.15 d 〇〇Em 0.T6 294 143 ◎ 〇〇0.16 Θ 〇〇0.1ft '331 170 〇〇0.17 & 〇〇ΓΜ Q.19 © 385 186 © 〇〇0.18 〇〇EH 0.1β 309 139 Θ 〇〇 0.18 & 〇〇Em 0.16 305 146 Θ 〇〇 0.16 Θ 〇〇 EM 0.16 314 145 Θ 〇〇 0.15 〇〇〇 0.17 ❺ 318 155 Θ 〇〇 0.17 ❺ 〇〇 ES 0.18 305 144 @ 〇〇 0.18 © 〇〇wm aie 222 108 〇〇0.15 〇〇E· 0.1β © 307 145 〇〇0.18 〇〇0.15 171 69 〇〇〇0.15 © 〇〇一— - - — — — — — 0.17 322 160 〇X 0.17 〇 X EX 0.17 Ο 306 150 Θ 〇X 0.16 〇 X 0.18 〇320 163 ύ 〇〇0.18 〇〇ΕΏ an €) 324 162 & 〇X 0.17 ❹ 〇X 0.18 322 158 0 〇X 0,17 〇X Eia 0.17 €> 305 146 θ 〇〇0.17 ❺ 〇〇 0.18 €> 310 147 〇〇〇0.18 〇〇EM 0.1$ 215 101 ο 〇〇0.14 ❽ 〇〇E9I wm 0.1$ ◎ 94 38 〇〇0.15 〇〇0.16 ρ 103 41 〇〇0.15 & 〇〇EBC 0.16 84 37 ❽ 〇〇 0.16 〇〇 gyc 0.17 117 49 〇X 0.16 d 〇X wm 0.1$ €> 92 37 〇〇0.H 〇〇适««外-33- 201006578 [ε揪] Color after treatment The surface properties of the spot 〇ο 0 o 〇ooooooo 0 IXX o XX ο 0 0 0 ο ο X Ο 1黯馥XXXXXXXXXXXXXIXXXXXXX ο XXXX 铝合金 Aluminum alloy hot plate 1111 XXXXXXXXXXXXXIXXXXXXX XXXXXX Strength (N/mm2) Endurance g S ss 'Si CM In 5? csl CM in «Μ 〇I <D CO 卜CO s 5i extract 5 3 LO ιη C0 ιη «ο ιτ> ιη tensile strength eg CVI CSJ 筘c〇 00 Oi eg Oi CM bag R 丨 2 97__I Oi o Another in I CM o a> CM «μ m evi Iso 1 28β 2 CNJ τ» 〇2 00 <0 β> CM ί Accuracy ◎ © ooo ◎ 〇oo 〇◎ o ◎ I © o ο ◎ ο ο ◎ ◎ © ο ◎ ο ◎ Flatness (mm/m) 0.41 1 I 0 *2 I 0.50 II 0.62 I 0.69 I 0.47 II 048 | I 0 47 I 0.50 0.48 I 0.43 II 0.49 II 0.42 II 1 0.48 1 1 0.50 1 0.49 1 〇·*8 1 0.48 1 0.50 1 1 0.50 1 0.40 1 0.41 I 0.42 I 0.41 I 0.44 I 0.41 Ming alloy _ Smoothing treatment by hairline processing Acid resistance After surface treatment due to the surface properties of the stain ο oo O ooooo 〇〇o IXX ο XX ο ο ο ο ο ο X ο 雄 IK 翡 EN XXXXXXXXXXXXXXXXXXXXXX ο XXXX ο SI ο 0 ooooo 〇o 0 ooo I 〇o ο Ο ο ο ο 0 ο ο ο ο ο ο S Accuracy ◎ ◎ Ooo ◎ 0 oo 0 © o ◎ 1 © o ο ◎ 0 ο ο ◎ ◎ ο ◎ ο ◎ Flatness (mm/m) 0-41 II 0-4t | I 0.50” 0.61 II 0.68 II 047 | 丨0-48 II 0-47 II 0.49 II 0-48 i I 0.43 I 0-48 | I 0.42 | 1 1 0 48 1 1 0.50 1 0.48 ! 1 0.48 1 1 0.47 1 1 0.50 1 I 0.49 1 1 0 .40 1 0.41 I 0.41 1 0.41 ]0.43 1 0.41 Alloy 6 5 ΙΛ 5 ίο in i5 in' ίο ΰ5 I 5fTVK 5n * 5o *1 * in * 5r* 5s* 5t* 1 5u * 1Π <s I 3c * 3d * -34- 201006578 Aluminium alloy thick plate formed of alloy Nos. 5a to 51 and 5v, the content of the additive element is within an appropriate range, and the surface is subjected to appropriate smoothing treatment, strength, flatness, Plate thickness accuracy and surface properties are good. 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 the alloy No. 5 m, since the Mg content is insufficient, sufficient strength cannot be obtained. Further, in the aluminum alloy thick plate formed of the alloy No. 5n, when the Mg content φ is excessive, the casting fracture 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 content of Cu, Zn, and Ti in the aluminum alloy thick plate formed of the alloy No. 5q, 5t, and 5u is larger than the appropriate range, compared with the alloy 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 from the hairline processing with a small amount of removal Φ, it is confirmed that the end milling cutter 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, 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 + hairline processing -35-201006578, it is confirmed that the black can be prevented due to the appropriate removal amount. Lines are produced. Further, when the aluminum alloy thick plate formed of 5v does not use Ti-B of the ingot refining agent at the time of slurry formation, it is not affected by the difference of the surface smoothing treatment method, and the surface smoothing treatment is confirmed. The method can prevent black lines from being generated. The aluminum alloy thick plate formed of the alloy Nos. 3a, 3b, and 3e has a content of an additive element in an appropriate range, and is subjected to appropriate smoothing treatment on the surface, strength, flatness, thickness accuracy, and surface properties. good. Moreover, sufficient strength and good surface properties can be obtained when compared with an 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. 3c, since the content of Μη is insufficient, sufficient strength cannot be obtained. Further, in the aluminum alloy thick plate formed of 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. Further, the difference in the method relating to the surface smoothing treatment can be performed when the end mill processing + hairline processing with the appropriate amount is removed, or when only the end mill processing is performed, compared to the hairline processing with only a small amount of removal. Confirm that the surface properties of the crucible are increased. Further, in the conventional hot-rolled plate, there is a flaw in the cut plate, 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, the 'line-only processing' can also confirm the effect of easily distinguishing functional defects. 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 + hairline processing -36-201006578, because the removal amount is appropriate 'confirmation can prevent black Lines are produced. Further, the aluminum alloy thick plate formed by 3e is not affected by the difference in the method of the surface smoothing treatment when the slurry ingot is not used in the case of the Ti-B of the ingot refining agent, 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 φ 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 alloy) The alloy of the composition of Alloy No. 6a to 6g shown in Table 4 was dissolved, dehydrogenated, filtered, and cast. , making an ingot with 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 rolled 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 -37-201006578 to add 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 used 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 is the same as in the case of the aforementioned A1-Mg alloy. Further, the obtained aluminum alloy thick plate was subjected to melt treatment at 520 ° 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之組成的鋁合金熔解，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1000mm後，對壓延面（兩面）而 言進行平滑化處理，形成厚度20mm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 - 201006578 下實施時效處理48小時。 【表4】 絕^質量％) No. M押 Si Fe Cu Mn Cr Zn Ti Zr Al** 6a 0.9 0.5 0.5 0.3 0.1 0.2 0.2 0.02 - 费留成分 6b 0.5 0.9 0.2 - 0.1 - - 0.02 - 贐留成分 6c本 0·9 0.1* 0.5 - 0.1 一 - 0.02 - 寖留成分 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 - 窺留成分 6f* 1.7* 0.5 0.4 - 0.1 一 - 0.02 - 殲留成分 6s 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 - 贿成分 7b 3.5 0.2 0.2 2.0 一 - 8.0 0.02 0.2 贿成分 7c* 0.3* 0.1 0.2 2.2 - 0.1 4.0 0.02 - 费留成分 7d* 5.0* 0.2 0.2 2.0 - 0.1 5.0 0.02 一 9留成分 7e * 2-5 0.1 0.2 2.2 - 0.1 2.4* 0.02 - 贿成分 7f* 3.0 0.2 0.2 2.0 一 0.1 9.5* 0.02 一 殯留成分 7g 2.5 0.1 0.2 1.8 - 0.2 4.0* — - 残留成分 *:適當範圍外神:含有不可避免的雜質 [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200N/mm2以上、合金No.7a〜7g (Al-Zn-Mg系合金），拉伸強度爲250N/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 - 201006578 【表5】The aluminum alloy having the composition of 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 1000 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 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. 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 - 201006578 for 48 hours. [Table 4] ^^质量%) No. M SiSi Fe Cu Mn Cr Zn Ti Zr Al** 6a 0.9 0.5 0.5 0.3 0.1 0.2 0.2 0.02 - Remaining component 6b 0.5 0.9 0.2 - 0.1 - - 0.02 - retention component 6c this 0·9 0.1* 0.5 - 0.1 a - 0.02 - leaching 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 - peeping component 6f* 1.7* 0.5 0.4 - 0.1 a - 0.02 - retention component 6s 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 - bribe ingredients 7b 3.5 0.2 0.2 2.0 one - 8.0 0.02 0.2 bribe ingredients 7c* 0.3 * 0.1 0.2 2.2 - 0.1 4.0 0.02 - Remaining component 7d* 5.0* 0.2 0.2 2.0 - 0.1 5.0 0.02 1 9 Residue 7e * 2-5 0.1 0.2 2.2 - 0.1 2.4* 0.02 - Bribe ingredient 7f* 3.0 0.2 0.2 2.0 0.1 9.5* 0.02 A retention component 7g 2.5 0.1 0.2 1.8 - 0.2 4.0* — - Residual composition*: Appropriate range outside God: contains unavoidable impurities [Example 2: Evaluation] On the obtained aluminum alloy thick plate, The strength and surface properties were evaluated in the same manner as in Example 1. 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. The basis of the strength is the alloy No. 6a to 6g (Al~Mg~Si alloy), the tensile strength is 200N/mm2 or more, the alloy No.7a~7g (Al-Zn-Mg alloy), and the tensile strength is 250N/mm2 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 - 201006578 [Table 5]
鋁合錄板 合金 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 平滑她理 No. 強度(N/mm2) 耐賴處理後 耐關處理後 拉伸強度 耐力 因勒莊之 表面性質 因黑色線條 之表面性質 因色斑之 表面tts 因瑕疵之 表面ttJf 因黑色線條 之表面性質 因之 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 6f， 210 124 〇 〇 ◎ 〇 〇 7a 321 273 © 〇 〇 〇 〇 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， 610 530 @ 〇 X © 〇 X 7ff 423 363 ◎ 〇 X @ 〇 X *:適當範外 【表6】Aluminium splicing plate alloy is smoothed by end sharp knife processing. Smoothing by end sharp knife processing + hairline processing. No. Strength (N/mm2) Tensile strength after endurance treatment The surface properties of Lezhuang due to the surface properties of black lines due to the surface of the stains tts due to the surface ttJf due to the surface properties of the black lines due to the surface properties 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© 〇〇6f, 210 124 〇〇◎ 〇〇7a 321 273 © 〇〇〇〇424 364 © 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, 610 530 @ 〇X © 〇X 7ff 423 363 ◎ 〇X @ 〇X *: Appropriate range [Table 6]
No. 鋁合金厚板 鋁合金熱延板 藉由髮線加工之平滑化處理 耐酸绍處理厚 強度(N/mm2〉 耐齡處理厚 因職之 表面性質 因黑線條之 表面性質 因顿之 表面性質 拉伸強度 耐力 因瑕庇之 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 * 0 X 〇 234 145 X X 〇 6g 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 0 X *:逋當範圍外 由合金No.6a,6b,6g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- 201006578 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所形成的銘合金厚板，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.6f所形成的鋁合金厚板’由於 Mg之含量過剩，由於形成ANMg系（ 5000系A1)合金之特 φ 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N〇.6a，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 φ 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 - 201006578 色線條產生。 由合金No. 7a、7b、7g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N〇.7d,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- 201006578 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]係爲習知技術之銘合金厚板的製造方法例之流 程圖。No. Aluminum alloy thick plate aluminum alloy hot-draw plate is smoothed by hairline processing and is resistant to acid and soaking. Thickness (N/mm2> Ageing treatment Thick surface properties due to the surface properties of black lines Tensile strength endurance due to the surface properties of the dark 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 * 0 X 〇234 145 XX 〇6g 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 0 X *: The outer range is made of alloy No. 6a, 6b, 6g formed aluminum alloy thick plate, the content of the added elements is within an appropriate range, due to the appropriate smoothing treatment on the surface, the strength and surface properties are good, and 'with -40- without smoothing treatment 201006578 Aluminum alloy hot plate phase In the case of the ratio, sufficient strength and good surface properties are obtained. In this case, the aluminum alloy thick plate formed by the alloy No. 6c, 6e is insufficient in the content of Si and Mg, and sufficient strength cannot be obtained. 'Ming alloy thick plate formed of alloy No. 6d, when a large Si content is formed, 'will form a large intermetallic compound', which produces a stain on the surface appearance after the alumite treatment. Moreover, it is formed by alloy No. 6f. Due to the excessive content of Mg in the aluminum alloy thick plate, due to the special φ nature of the alloy formed by the ANMg system (5000 series A1), the effect of improving the strength cannot be obtained by the melt treatment and the effect of the Mg, and the content of Mg is appropriate. When the alloys in the range N〇.6a, 6b are compared, there is a case where the strength is lowered. In addition, the method for the surface smoothing treatment differs, and the removal amount is appropriate when compared with the hair removal processing with a small amount of removal. When the end mill processing + hairline processing, or only the end mill processing, it is confirmed that the surface properties of the crucible are improved. Moreover, there are flaws on the cut sheet of the conventional heat extension sheet, including visible to the naked eye. Dimensional work φ off by no problem of the minute defect determination, only the hair line process of the cutting board seen flaws, defects may be visually apparent determination. 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 - 201006578 color lines from being produced. The aluminum alloy thick plate formed of Alloy Nos. 7a, 7b, and 7g has an appropriate content in the range of the added element, and is excellent in strength and surface properties by performing appropriate smoothing treatment on the surface. 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 the alloys N〇.7d and 7f, since the content of Mg and Zn is excessive, coarse intermetallic compounds are formed, and stains appear on the surface appearance after the alumite treatment. 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, the aluminum alloy thick plate formed of 7 g is not affected by the difference in the method of the surface smoothing treatment when Ti-B of the ingot refining agent is not used in the slurry agglomeration, and the surface smoothing treatment is confirmed. The method can prevent the black line from producing -42- 201006578. 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 a thick alloy plate of the prior art.
-43--43-
Claims (1)
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2008085283 | 2008-03-28 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| TW201006578A true TW201006578A (en) | 2010-02-16 |
| TWI355301B TWI355301B (en) | 2012-01-01 |
Family
ID=41113912
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| TW98110134A TWI355301B (en) | 2008-03-28 | 2009-03-27 | Aluminum alloy thick plate and method for manufact |
Country Status (6)
| Country | Link |
|---|---|
| EP (1) | EP2263811A4 (en) |
| JP (1) | JP4410835B2 (en) |
| KR (1) | KR101251235B1 (en) |
| CN (1) | CN101959625A (en) |
| TW (1) | TWI355301B (en) |
| WO (1) | WO2009119724A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113798321A (en) * | 2021-09-11 | 2021-12-17 | 百色学院 | Aluminum alloy thick plate and manufacturing method thereof |
Families Citing this family (30)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR101248234B1 (en) * | 2010-12-23 | 2013-04-02 | 이희만 | One-stop production system for steel pallets |
| CN103173629A (en) * | 2011-12-23 | 2013-06-26 | 秦皇岛开发区美铝合金有限公司 | Aluminum alloy cleanliness treatment process special for hub forging |
| CN102553917A (en) * | 2012-02-17 | 2012-07-11 | 西南铝业（集团）有限责任公司 | Production method of aluminium alloy sheets |
| CN102634686B (en) * | 2012-03-13 | 2014-10-08 | 浙江永杰铝业有限公司 | Casting method of aluminum alloy for ship |
| EP2653577B2 (en) * | 2012-04-20 | 2023-02-15 | UACJ Corporation | Method for producing an aluminum alloy sheet that exhibits excellent surface quality after anodizing |
| US10415118B2 (en) | 2012-06-15 | 2019-09-17 | Uacj Corporation | Aluminum alloy plate |
| JP5944862B2 (en) * | 2012-08-08 | 2016-07-05 | 株式会社Uacj | Aluminum alloy plate excellent in surface quality after anodizing treatment and manufacturing method thereof |
| US9315885B2 (en) * | 2013-03-09 | 2016-04-19 | Alcoa Inc. | Heat treatable aluminum alloys having magnesium and zinc and methods for producing the same |
| CN103436755B (en) * | 2013-08-23 | 2015-09-23 | 北京艾路浦科技发展有限公司 | A kind of rust-preventing aluminum alloy material |
| CN103484736B (en) * | 2013-10-10 | 2016-05-11 | 东北大学 | Strong 6000 line aluminium alloys of a kind of superelevation and preparation method thereof |
| CN104988360A (en) * | 2015-05-29 | 2015-10-21 | 柳州普亚贸易有限公司 | High-strength corrosion resistance aluminum alloy for door and window |
| CN108138269A (en) | 2015-12-18 | 2018-06-08 | 诺维尔里斯公司 | High intensity 6XXX aluminium alloys and preparation method |
| KR102228792B1 (en) | 2015-12-18 | 2021-03-19 | 노벨리스 인크. | High strength 6XXX aluminum alloys and methods of making them |
| KR101816202B1 (en) * | 2015-12-31 | 2018-01-09 | 최창민 | Aluminum alloy for high strength |
| CN105543520B (en) * | 2015-12-31 | 2017-11-03 | 广西南南铝加工有限公司 | A kind of preparation method of electronic product casing aluminum alloy base material |
| CN107287478A (en) * | 2017-05-26 | 2017-10-24 | 温州兴锐成科技有限公司 | A kind of aluminium Y-tooth line and preparation method thereof |
| CN107557624B (en) * | 2017-08-29 | 2019-03-26 | 河南明泰科技发展有限公司 | A kind of aluminium alloy container aluminium sheet and its production method |
| CN107541623A (en) * | 2017-08-30 | 2018-01-05 | 宁波华源精特金属制品有限公司 | A kind of sway bar |
| WO2019222236A1 (en) | 2018-05-15 | 2019-11-21 | Novelis Inc. | High strength 6xxx and 7xxx aluminum alloys and methods of making the same |
| CN108715958A (en) * | 2018-05-30 | 2018-10-30 | 澳洋集团有限公司 | A kind of magnesium-aluminium alloy material and preparation method thereof |
| JP6492218B1 (en) * | 2018-07-25 | 2019-03-27 | 株式会社Uacj | Aluminum alloy plate for magnetic disk, method of manufacturing the same, and magnetic disk using this aluminum alloy plate for magnetic disk |
| CN109596711B (en) * | 2019-01-10 | 2021-12-28 | 无锡透平叶片有限公司 | Method for detecting metallurgical defects of large-size cast aluminum alloy |
| EP3956488A4 (en) * | 2019-04-19 | 2022-12-21 | Magna International Inc | Non-heat-treated casting alloys for automotive structural applications |
| FR3101641B1 (en) | 2019-10-04 | 2022-01-21 | Constellium Issoire | Aluminum alloy precision sheets |
| CN111534729B (en) * | 2020-06-11 | 2022-05-10 | 东北轻合金有限责任公司 | Method for controlling transverse unevenness of high-strength aluminum alloy plate |
| CN113751503A (en) * | 2021-08-19 | 2021-12-07 | 山东南山铝业股份有限公司 | Welding method of 7-series aluminum alloy clad thin plate for aviation |
| CN114457264A (en) * | 2022-01-28 | 2022-05-10 | 邹平宏发铝业科技有限公司 | 5-series aluminum alloy strip for stamping lamp and processing method thereof |
| FR3136242B1 (en) | 2022-06-01 | 2024-05-03 | Constellium Valais | Sheet metal for vacuum chamber elements made of aluminum alloy |
| CN115029592B (en) * | 2022-06-14 | 2023-12-01 | 天津忠旺铝业有限公司 | Production method of 5052-H32 aluminum alloy plate for automobile structural part |
| CN115786749A (en) * | 2022-12-23 | 2023-03-14 | 苏州宇上实业有限公司 | 5-series aluminum alloy plate and preparation method thereof |
Family Cites Families (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5118252A (en) * | 1974-08-06 | 1976-02-13 | Nippon Kokan Kk | Atsuenkinzokubanno choryokubunpunyoru keijoseigyoho |
| US4406717A (en) * | 1980-12-23 | 1983-09-27 | Aluminum Company Of America | Wrought aluminum base alloy product having refined Al-Fe type intermetallic phases |
| JPH0245925B2 (en) | 1986-10-31 | 1990-10-12 | Kobe Steel Ltd | KINZOKUSEIDAIBANSHIITOZAINOSHODONHOHO |
| JPH06218495A (en) * | 1992-09-03 | 1994-08-09 | Fuji Photo Film Co Ltd | Manufacture of supporting body for planographic printing plate |
| US5338510A (en) * | 1993-10-04 | 1994-08-16 | Zuech Romeo A | Cast aluminum alloy and tooling fixture therefrom |
| JP3549080B2 (en) * | 1996-08-06 | 2004-08-04 | 富士写真フイルム株式会社 | Method and apparatus for manufacturing a lithographic printing plate support |
| JPH10137814A (en) * | 1996-11-11 | 1998-05-26 | Kawasaki Steel Corp | Surface cutting device of hot plate stock |
| JP2000219996A (en) * | 1999-02-01 | 2000-08-08 | Kobe Steel Ltd | Production of copper or copper alloy sheet for electronic parts |
| JP2001335812A (en) * | 2000-03-24 | 2001-12-04 | Senju Metal Ind Co Ltd | Lead-free plain bearing and its production method |
| JP2002146447A (en) | 2000-11-01 | 2002-05-22 | Daido Steel Co Ltd | Degassing apparatus for non-ferrous metal |
| JP2005074453A (en) * | 2003-08-29 | 2005-03-24 | Nippon Light Metal Co Ltd | Method for producing aluminum alloy thick plate |
| JP4616684B2 (en) | 2005-03-31 | 2011-01-19 | 株式会社神戸製鋼所 | Suction pad and plate inspection equipment |
| JP2006316332A (en) | 2005-05-16 | 2006-11-24 | Sumitomo Light Metal Ind Ltd | Aluminum alloy sheet material having excellent drawing formability, and method for producing the same |
| KR101197952B1 (en) * | 2007-03-30 | 2012-11-05 | 가부시키가이샤 고베 세이코쇼 | Method for producing aluminum alloy thick plate and aluminum alloy thick plate |
-
2009
- 2009-03-02 JP JP2009048470A patent/JP4410835B2/en not_active Expired - Fee Related
- 2009-03-26 EP EP09726074A patent/EP2263811A4/en not_active Withdrawn
- 2009-03-26 KR KR1020107021535A patent/KR101251235B1/en active IP Right Grant
- 2009-03-26 CN CN200980106340XA patent/CN101959625A/en active Pending
- 2009-03-26 WO PCT/JP2009/056089 patent/WO2009119724A1/en active Application Filing
- 2009-03-27 TW TW98110134A patent/TWI355301B/en not_active IP Right Cessation
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113798321A (en) * | 2021-09-11 | 2021-12-17 | 百色学院 | Aluminum alloy thick plate and manufacturing method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| TWI355301B (en) | 2012-01-01 |
| JP2009256782A (en) | 2009-11-05 |
| KR101251235B1 (en) | 2013-04-08 |
| JP4410835B2 (en) | 2010-02-03 |
| WO2009119724A1 (en) | 2009-10-01 |
| EP2263811A4 (en) | 2011-05-04 |
| EP2263811A1 (en) | 2010-12-22 |
| CN101959625A (en) | 2011-01-26 |
| KR20100116698A (en) | 2010-11-01 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| TW201006578A (en) | Aluminum alloy thick plate and method for manufacturing the same | |
| CN1136329C (en) | Damage tolerant aluminium alloy product and method of its manufacture | |
| KR20150046067A (en) | Aluminum alloy foil with excellent formability after laminating, process for producing same, and laminated foil obtained using said aluminum alloy foil | |
| JP2009533223A (en) | Cladding superplastic alloy | |
| JP6336434B2 (en) | Aluminum alloy plate for can body and manufacturing method thereof | |
| CN103526079A (en) | A can aluminum alloy plate and a manufacturing method thereof | |
| JP6169950B2 (en) | Aluminum alloy substrate for magnetic disk | |
| JP2014074213A (en) | High strength aluminum alloy extruded material and method of producing the same | |
| CN105324500A (en) | Aluminum alloy plate for magnetic disk, aluminum alloy blank for magnetic disk, and aluminum alloy substrate for magnetic disk | |
| FR3053979B1 (en) | FLANS IN ALUMINUM ALLOYS WITH A LOCAL FLASH RECLA | |
| CN105316545A (en) | Rolled aluminum alloy material | |
| CA2588046C (en) | Aluminum alloy sheet and method for manufacturing the same | |
| TWI468527B (en) | Method for fabricating aluminum alloy thick plate and aluminum alloy thick plate | |
| JP6792463B2 (en) | Aluminum alloy soft foil for molding | |
| CN108884520A (en) | Disk aluminium alloy green body and disk aluminium alloy substrate | |
| JP2007186747A (en) | Aluminum alloy material to be formed at high temperature and a high speed, manufacturing method therefor and method for manufacturing formed article from aluminum alloy | |
| JP3787695B2 (en) | Aluminum alloy foil and method for producing the same | |
| JP4712159B2 (en) | Aluminum alloy plate excellent in strength and corrosion resistance and method for producing the same | |
| JP7414453B2 (en) | Aluminum alloy material and its manufacturing method | |
| JP6466316B2 (en) | Aluminum alloy hard foil and method for producing the same | |
| JP6674362B2 (en) | Aluminum alloy foil and method for producing the same | |
| JPH09268341A (en) | Baking-coated al alloy sheet for can lid material, excellent in stress corrosion cracking resistance in score part, and its production | |
| Sadeghi et al. | Effect of tool offset on microstructure and mechanical properties of dissimilar copper-brass friction stir welding | |
| CN114807688B (en) | 6-series aluminum alloy plate strip with high durability for automobile body and preparation method thereof | |
| JP2007154273A (en) | Aluminum alloy sheet with little cut-powder at the time of shearing and shearing-processing method therefor |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| MM4A | Annulment or lapse of patent due to non-payment of fees |