TW201738390A - Method for producing al-mg-Si alloy plate - Google Patents
Method for producing al-mg-Si alloy plate Download PDFInfo
- Publication number
- TW201738390A TW201738390A TW106103837A TW106103837A TW201738390A TW 201738390 A TW201738390 A TW 201738390A TW 106103837 A TW106103837 A TW 106103837A TW 106103837 A TW106103837 A TW 106103837A TW 201738390 A TW201738390 A TW 201738390A
- Authority
- TW
- Taiwan
- Prior art keywords
- producing
- alloy sheet
- based alloy
- sheet according
- heat treatment
- Prior art date
Links
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 126
- 229910021365 Al-Mg-Si alloy Inorganic materials 0.000 title claims abstract description 102
- 239000000956 alloy Substances 0.000 claims abstract description 223
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 222
- 238000005098 hot rolling Methods 0.000 claims abstract description 179
- 238000005097 cold rolling Methods 0.000 claims abstract description 117
- 238000010438 heat treatment Methods 0.000 claims abstract description 112
- 229910018464 Al—Mg—Si Inorganic materials 0.000 claims description 159
- 238000000137 annealing Methods 0.000 claims description 51
- 238000001816 cooling Methods 0.000 claims description 50
- 238000000034 method Methods 0.000 claims description 46
- 239000012535 impurity Substances 0.000 claims description 35
- 238000005096 rolling process Methods 0.000 claims description 33
- 239000000203 mixture Substances 0.000 claims description 17
- 239000000126 substance Substances 0.000 claims description 15
- 229910052804 chromium Inorganic materials 0.000 claims description 12
- 229910052748 manganese Inorganic materials 0.000 claims description 11
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 10
- 229910052725 zinc Inorganic materials 0.000 claims description 9
- 229910052719 titanium Inorganic materials 0.000 claims description 8
- 229910052797 bismuth Inorganic materials 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- 229910052718 tin Inorganic materials 0.000 claims description 4
- 229910052720 vanadium Inorganic materials 0.000 claims description 4
- 229910052726 zirconium Inorganic materials 0.000 claims description 4
- 229910019064 Mg-Si Inorganic materials 0.000 claims description 3
- 229910019406 Mg—Si Inorganic materials 0.000 claims description 3
- 230000001747 exhibiting effect Effects 0.000 abstract 1
- 230000002349 favourable effect Effects 0.000 abstract 1
- 229910000838 Al alloy Inorganic materials 0.000 description 19
- 229910000831 Steel Inorganic materials 0.000 description 14
- 239000010949 copper Substances 0.000 description 14
- 230000000171 quenching effect Effects 0.000 description 14
- 239000010959 steel Substances 0.000 description 14
- 238000005452 bending Methods 0.000 description 11
- 238000000265 homogenisation Methods 0.000 description 11
- 230000000052 comparative effect Effects 0.000 description 7
- 239000013078 crystal Substances 0.000 description 7
- 230000000694 effects Effects 0.000 description 7
- 238000005266 casting Methods 0.000 description 6
- 238000005520 cutting process Methods 0.000 description 6
- 238000005336 cracking Methods 0.000 description 5
- 238000012545 processing Methods 0.000 description 5
- 239000000047 product Substances 0.000 description 5
- 238000010791 quenching Methods 0.000 description 5
- 229910052802 copper Inorganic materials 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 239000000243 solution Substances 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 3
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 3
- 229910052737 gold Inorganic materials 0.000 description 3
- 239000010931 gold Substances 0.000 description 3
- 210000001161 mammalian embryo Anatomy 0.000 description 3
- 229910018134 Al-Mg Inorganic materials 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 2
- 229910018467 Al—Mg Inorganic materials 0.000 description 2
- 229910001339 C alloy Inorganic materials 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 238000003490 calendering Methods 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 230000014509 gene expression Effects 0.000 description 2
- 239000007769 metal material Substances 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000005507 spraying Methods 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 238000010998 test method Methods 0.000 description 2
- 238000004804 winding Methods 0.000 description 2
- 229910001152 Bi alloy Inorganic materials 0.000 description 1
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 1
- AYCPARAPKDAOEN-LJQANCHMSA-N N-[(1S)-2-(dimethylamino)-1-phenylethyl]-6,6-dimethyl-3-[(2-methyl-4-thieno[3,2-d]pyrimidinyl)amino]-1,4-dihydropyrrolo[3,4-c]pyrazole-5-carboxamide Chemical compound C1([C@H](NC(=O)N2C(C=3NN=C(NC=4C=5SC=CC=5N=C(C)N=4)C=3C2)(C)C)CN(C)C)=CC=CC=C1 AYCPARAPKDAOEN-LJQANCHMSA-N 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000003483 aging Methods 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 239000002826 coolant Substances 0.000 description 1
- 238000012217 deletion Methods 0.000 description 1
- 230000037430 deletion Effects 0.000 description 1
- 238000000151 deposition Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 230000002431 foraging effect Effects 0.000 description 1
- 230000017525 heat dissipation Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 150000002910 rare earth metals Chemical class 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000012552 review Methods 0.000 description 1
- 229910052709 silver Inorganic materials 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
-
- 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
-
- 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
- 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
- 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
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Metal Rolling (AREA)
- Conductive Materials (AREA)
Abstract
Description
本發明係關於Al-Mg-Si系合金板之製造方法，特別是關於熱傳導性、導電性、強度及加工性優異之Al-Mg-Si系合金板之製造方法。 The present invention relates to a method for producing an Al-Mg-Si-based alloy sheet, and more particularly to a method for producing an Al-Mg-Si-based alloy sheet excellent in thermal conductivity, electrical conductivity, strength, and workability.
在如薄型電視、個人電腦用薄型顯示器、筆記型電腦、平板電腦、汽車導航系統、攜帶式導航系統、智慧型手機或手機等的攜帶式終端等製品的框架、金屬基印刷電路板、內蓋之內藏或裝著散熱體的構件材料中，追求為了快速散熱的優異熱傳導性、強度及加工性。 Frames, metal-based printed circuit boards, and inner covers for products such as thin-type TVs, thin-type displays for personal computers, notebook computers, tablet computers, car navigation systems, portable navigation systems, smart phones, or mobile phones Among the component materials in which the heat sink is housed or contained, excellent heat conductivity, strength, and workability for rapid heat dissipation are pursued.
JIS1100、1050、1070等純鋁合金雖熱傳導性優異但強度低。而用作高強度材料的JIS5052等Al-Mg合金(5000系合金)相較於純鋁系合金，其熱傳導性及導電性顯著較差。 Pure aluminum alloys such as JIS1100, 1050, and 1070 have excellent thermal conductivity but low strength. Al-Mg alloys (5000 series alloys) such as JIS 5052 used as high-strength materials have significantly lower thermal conductivity and electrical conductivity than pure aluminum-based alloys.
相對於此，由於Al-Mg-Si系合金(6000系合金)可謀求良好熱傳導性及導電性且藉由時效硬化而強度提升，故探討使用Al-Mg-Si系合金以得到強度、熱傳導性及加工性優異之鋁合金板的方法。 On the other hand, since the Al—Mg—Si-based alloy (6000-based alloy) can improve the thermal conductivity and conductivity and improve the strength by age hardening, it is considered to use an Al—Mg—Si-based alloy to obtain strength and thermal conductivity. And a method of an aluminum alloy sheet excellent in workability.
例如，專利文獻1揭示有一種Al-Mg-Si系合金壓延板之製造方法，其特徵為將含有Mg 0.1~0.34質量%、Si 0.2~0.8質量%、Cu 0.22~1.0質量%，剩餘部分由Al及不可避免的雜質構成，Si/Mg含量比為1.3以上的Al-Mg-Si系合金以半連續鑄造做成厚度250mm以上的鑄錠，並用400~540℃的溫度進行預備加熱後熱軋，再以50~85%的壓下率施以冷軋後，以140~280℃的溫度來退火。 For example, Patent Document 1 discloses a method for producing an Al-Mg-Si-based alloy rolled sheet, which is characterized in that it contains Mg 0.1 to 0.34% by mass, Si 0.2 to 0.8% by mass, and Cu 0.22 to 1.0% by mass, and the remainder is Al and an unavoidable impurity structure, an Al-Mg-Si alloy having a Si/Mg content ratio of 1.3 or more is semi-continuously cast into an ingot having a thickness of 250 mm or more, and is subjected to preliminary heating and hot rolling at a temperature of 400 to 540 °C. Then, after cold rolling at a reduction ratio of 50 to 85%, annealing is performed at a temperature of 140 to 280 °C.
專利文獻2記載有一種熱傳導性、強度及彎曲加工性優異之鋁合金板之製造方法，其特徵為將具有含有Si：0.2~1.5質量%、Mg：0.2~1.5質量%、Fe：0.3質量%以下，進而在含有Mn：0.02~0.15質量%、Cr：0.02~0.15%中之1種或2種，同時剩餘部分為Al及不可避免雜質中的Ti為規範在0.2%以下；又或其中含Cu：0.01~1質量%或稀土類元素：0.01~0.2質量%中之1種或2種之組成的鋁合金板藉由連續鑄造壓延來製作，而後冷軋，接著以500~570℃實施溶體化處理，繼續以冷軋率5~40%進行冷軋，冷軋後再進行加熱至150~未達190℃之時效處理。 Patent Document 2 describes a method for producing an aluminum alloy sheet excellent in thermal conductivity, strength, and bending workability, and is characterized in that it contains Si: 0.2 to 1.5% by mass, Mg: 0.2 to 1.5% by mass, and Fe: 0.3% by mass. In addition, one or two types of Mn: 0.02 to 0.15 mass% and Cr: 0.02 to 0.15% are contained, and the balance of Ti in the remaining portion of Al and inevitable impurities is 0.2% or less; or Cu: 0.01 to 1% by mass or a rare earth element: an aluminum alloy sheet of one or two of 0.01 to 0.2% by mass is produced by continuous casting calendering, followed by cold rolling, followed by dissolution at 500 to 570 °C. The body treatment is continued with cold rolling at a cold rolling rate of 5 to 40%, and after cold rolling, heating to 150 to 190 ° C for aging treatment.
專利文獻3揭示有一種Al-Mg-Si系合金板之製造方法，其係包含將含有Si：0.2~0.8質量%、Mg：0.3~1質量%、Fe：0.5質量%以下、Cu：0.5質量%以下，進而含有Ti：0.1質量%以下或B：0.1質量%以下之至少1種，剩餘部分由Al及不可避免的雜質所構成，或進而作為雜質之Mn及Cr規範在Mn：0.1質量%以下、Cr：0.1質量%以下之Al-Mg-Si系合金鑄錠進行熱軋，進而進行冷軋的 步驟之合金板之製造方法，其特徵為在熱軋後至冷軋結束之間，藉由以200~400℃保持1小時以上進行熱處理。 Patent Document 3 discloses a method for producing an Al-Mg-Si-based alloy sheet comprising Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5 mass. % or less, further containing at least one of Ti: 0.1% by mass or less or B: 0.1% by mass or less, the remainder being composed of Al and unavoidable impurities, or further Mn and Cr as impurities are specified in Mn: 0.1% by mass. In the following, an Al-Mg-Si alloy ingot of Cr: 0.1% by mass or less is hot rolled and further cold rolled. The method for producing an alloy sheet according to the step is characterized in that heat treatment is carried out by holding at 200 to 400 ° C for 1 hour or more after hot rolling to the end of cold rolling.
此外，如專利文獻3所記載，在JIS1000系至7000系之鋁合金中，熱傳導率與導電率顯示良好的相關性，具有優異之熱傳導性的鋁合金板具有優異的導電率，當然可用作散熱構件材料亦可用作導電構件材料。 Further, as described in Patent Document 3, in the case of the JIS1000-based to 7000-series aluminum alloy, the thermal conductivity and the electrical conductivity show a good correlation, and the aluminum alloy sheet having excellent thermal conductivity has excellent electrical conductivity, and can of course be used. The heat dissipating member material can also be used as a conductive member material.
[專利文獻1]日本特開2012-62517號公報 [Patent Document 1] Japanese Patent Laid-Open Publication No. 2012-62517
[專利文獻2]日本特開2007-9262號公報 [Patent Document 2] Japanese Patent Laid-Open Publication No. 2007-9262
[專利文獻3]日本特開2003-321755號公報 [Patent Document 3] Japanese Patent Laid-Open Publication No. 2003-321755
然而，專利文獻1記載之製造方法所得的合金壓延板之拉伸強度的改善多為合金組成之原因，步驟條件的研討不充分。又，專利文獻1規定之合金壓延板之化學組成，相對地包含較多的Cu，較Al次多的元素為Si或Cu，Mg含量相對較少且不含以幾乎相同比例含有Si及Mg的合金。 However, the improvement of the tensile strength of the alloy rolled sheet obtained by the production method described in Patent Document 1 is mostly due to the alloy composition, and the study of the step conditions is insufficient. Further, the chemical composition of the alloy rolled sheet specified in Patent Document 1 relatively contains a large amount of Cu, and the element which is more than Al is Si or Cu, and the Mg content is relatively small and does not contain Si and Mg in almost the same ratio. alloy.
專利文獻2中，可得到具有對較高強度之鋁合金板的實施例所記載的導電率較專利文獻1記載之合金板低。又，專利文獻2中可得到高強度者為由在冷軋途中對鋁合 金板施以500℃以上的高溫熱處理及其後之急速冷卻而成 的溶體化處理後，進一步實施冷軋後再進行時效處理，但 藉由溶體化處理而成本變高。 In Patent Document 2, it is found that the electrical conductivity described in the examples of the aluminum alloy sheet having a higher strength is lower than that of the alloy sheet described in Patent Document 1. Further, in Patent Document 2, it is possible to obtain high strength for aluminum alloy in the course of cold rolling. The gold plate is subjected to high temperature heat treatment at 500 ° C or higher and then rapidly cooled. After the solution treatment, further cold rolling is performed and then aging treatment is performed, but The cost is increased by the solution treatment.
專利文獻3中，雖可得到較專利文獻1高強度之Al-Mg-Si系合金板，但未有關於熱軋之最終道次(相當於專利文獻3中之終熱軋)的研討，步驟條件的研討難以說是充分。 In Patent Document 3, an Al-Mg-Si alloy plate having a higher strength than that of Patent Document 1 is obtained, but the final pass of the hot rolling (corresponding to the final hot rolling in Patent Document 3) is not discussed. The study of conditions is hard to say is sufficient.
本發明之目的係鑑於上述之技術背景，提供一種在熱軋之後的步驟中不運用溶體化處理即可具有高導電率與良好的加工性並可進一步改善強度的Al-Mg-Si系合金板之製造方法。 The object of the present invention is to provide an Al-Mg-Si alloy which can have high electrical conductivity and good processability and can further improve strength without using a solution treatment in the step after hot rolling in view of the above technical background. The manufacturing method of the board.
上述課題藉由以下手段來解解決。 The above problems are solved by the following means.
(1)對Al-Mg-Si系合金鑄錠依序實施熱軋、冷軋的合金板之製造方法，其熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為230℃以下，且在熱軋結束後冷軋結束前以200℃以上400℃以下的溫度進行熱處理之Al-Mg-Si系合金板之製造方法。 (1) A method for producing an alloy sheet of hot-rolled or cold-rolled Al-Mg-Si alloy ingot, wherein the surface temperature of the Al-Mg-Si alloy sheet immediately after the hot rolling is 230 ° C or less And a method of producing an Al-Mg-Si-based alloy sheet which is heat-treated at a temperature of 200 ° C or more and 400 ° C or less before the end of cold rolling after the completion of hot rolling.
(2)Al-Mg-Si系合金鑄錠之化學組成係含有Si：0.2~0.8質量%、Mg：0.3~1質量%、Fe：0.5質量%以下及Cu：0.5質量%以下，剩餘部分由Al及不可避免的雜質所構成之如前項1所記載之Al-Mg-Si系合金板之製造方法。 (2) The chemical composition of the Al-Mg-Si alloy ingot contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less, and the balance is A method for producing an Al-Mg-Si alloy sheet according to the above item 1 comprising Al and unavoidable impurities.
(3)作為雜質之Mn、Cr、Zn、及Ti分別規範在0.1質量%以下之如前項1所記載之Al-Mg-Si系合金板之製造方法。 (3) A method for producing an Al-Mg-Si-based alloy sheet according to the above item 1 in which Mn, Cr, Zn, and Ti, which are impurities, are each specified to be 0.1% by mass or less.
(4)作為雜質之Mn、Cr、Zn、及Ti分別規範在0.1質量%以下之前項2所記載之Al-Mg-Si系合金板之製造方法。 (4) Mn, Cr, Zn, and Ti, which are impurities, are respectively specified to be 0.1% by mass or less of the method for producing an Al-Mg-Si-based alloy sheet according to Item 2.
(5)在熱軋結束後冷軋開始前實施熱處理之如前項1所記載之Al-Mg-Si系合金板之製造方法。 (5) A method for producing an Al-Mg-Si-based alloy sheet according to the above item 1 which is subjected to heat treatment before the start of cold rolling after completion of hot rolling.
(6)在熱軋結束後冷軋開始前實施熱處理之前項2所記載之Al-Mg-Si系合金板之製造方法。 (6) A method for producing an Al-Mg-Si-based alloy sheet according to Item 2 before the start of the heat treatment before the start of the cold rolling after the completion of the hot rolling.
(7)在熱軋結束後冷軋開始前實施熱處理之前項3所記載之Al-Mg-Si系合金板之製造方法。 (7) A method for producing an Al-Mg-Si-based alloy sheet according to Item 3 before the start of the heat treatment before the start of the cold rolling after the completion of the hot rolling.
(8)在熱軋結束後冷軋開始前實施熱處理之前項4所記載之Al-Mg-Si系合金板之製造方法。 (8) A method for producing an Al-Mg-Si-based alloy sheet according to Item 4 before the start of the heat treatment before the start of the cold rolling after the completion of the hot rolling.
(9)熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為200℃以下之前項5所記載之Al-Mg-Si系合金板之製造方法。 (9) The surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 200 ° C or less. The method for producing the Al-Mg-Si-based alloy sheet described in the above item 5.
(10)熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為200℃以下之前項6所記載之Al-Mg-Si系合金板之製造方法。 (10) The surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 200 ° C or less. The method for producing the Al-Mg-Si-based alloy sheet described in the above item 6.
(11)熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為200℃以下之前項7所記載之Al-Mg-Si系合金板之製造方法。 (11) A method for producing an Al-Mg-Si-based alloy sheet according to Item 7 after the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 200 ° C or lower.
(12)熱軋剛結束後之Al-Mg-Si系合金板的表面溫 度為200℃以下之前項8所記載之Al-Mg-Si系合金板之製造方法。 (12) Surface temperature of Al-Mg-Si alloy plate immediately after hot rolling The method of producing an Al-Mg-Si-based alloy sheet according to item 8 of 200 ° C or lower.
(13)熱處理溫度為200℃以上300℃以下之前項9所記載之Al-Mg-Si系合金板之製造方法。 (13) A method for producing an Al-Mg-Si-based alloy sheet according to item 9 of the heat treatment temperature of 200 ° C or more and 300 ° C or less.
(14)熱處理溫度為200℃以上300℃以下之前項10所記載之Al-Mg-Si系合金板之製造方法。 (14) A method for producing an Al-Mg-Si-based alloy sheet according to item 10, which has a heat treatment temperature of 200 ° C or more and 300 ° C or less.
(15)熱處理溫度為200℃以上300℃以下之前項11所記載之Al-Mg-Si系合金板之製造方法。 (15) A method for producing an Al-Mg-Si-based alloy sheet according to item 11 in which the heat treatment temperature is 200 ° C or more and 300 ° C or less.
(16)熱處理溫度為200℃以上300℃以下之前項12所記載之Al-Mg-Si系合金板之製造方法。 (16) A method for producing an Al-Mg-Si-based alloy sheet according to item 12, wherein the heat treatment temperature is 200 ° C or more and 300 ° C or less.
(17)熱處理後之冷軋之壓延率為20%以上之前項13所記載之Al-Mg-Si系合金板之製造方法。 (17) A method for producing an Al-Mg-Si-based alloy sheet according to Item 13, which has a rolling ratio of cold rolling after heat treatment of 20% or more.
(18)熱處理後之冷軋之壓延率為20%以上之前項14所記載之Al-Mg-Si系合金板之製造方法。 (18) A method of producing an Al-Mg-Si-based alloy sheet according to item 14 of the present invention, wherein the rolling ratio of the cold rolling after the heat treatment is 20% or more.
(19)熱處理後之冷軋之壓延率為20%以上之前項15所記載之Al-Mg-Si系合金板之製造方法。 (19) A method of producing an Al-Mg-Si-based alloy sheet according to item 15 of the first aspect, wherein the rolling ratio of the cold rolling after the heat treatment is 20% or more.
(20)熱處理後之冷軋之壓延率為20%以上之前項16所記載之Al-Mg-Si系合金板之製造方法。 (20) A method of producing an Al-Mg-Si-based alloy sheet according to item 16 of the present invention, wherein the rolling ratio of the cold rolling after the heat treatment is 20% or more.
(21)冷軋後實施最終退火之前項17所記載之Al-Mg-Si系合金板之製造方法。 (21) A method for producing an Al-Mg-Si-based alloy sheet according to Item 17 before final annealing after cold rolling.
(22)冷軋後實施最終退火之前項18所記載之Al-Mg-Si系合金板之製造方法。 (22) A method for producing an Al-Mg-Si-based alloy sheet according to Item 18 before final annealing after cold rolling.
(23)冷軋後實施最終退火之前項19所記載之Al-Mg-Si系合金板之製造方法。 (23) A method for producing an Al-Mg-Si-based alloy sheet according to Item 19 before final annealing after cold rolling.
(24)冷軋後實施最終退火之前項20所記載之Al-Mg-Si系合金板之製造方法。 (24) A method for producing an Al-Mg-Si-based alloy sheet according to Item 20 before final annealing after cold rolling.
(25)最終退火之溫度為200℃以下之前項21所記載之Al-Mg-Si系合金板之製造方法。 (25) The method of producing the Al-Mg-Si alloy sheet according to the above item 21, wherein the temperature of the final annealing is 200 ° C or lower.
(26)最終退火之溫度為200℃以下之前項22所記載之Al-Mg-Si系合金板之製造方法。 (26) The method of producing the Al-Mg-Si-based alloy sheet described in the above item 22, wherein the temperature of the final annealing is 200 ° C or lower.
(27)最終退火之溫度為200℃以下之前項23所記載之Al-Mg-Si系合金板之製造方法。 (27) The method of producing the Al-Mg-Si-based alloy sheet according to Item 23, which is a temperature at which the final annealing is 200 ° C or lower.
(28)最終退火之溫度為200℃以下之前項24所記載之Al-Mg-Si系合金板之製造方法。 (28) The method of producing the Al-Mg-Si-based alloy sheet according to Item 24, which is a temperature at which the final annealing is 200 ° C or lower.
(29)在熱軋之複數道次之中，至少實施1次道次前之Al-Mg-Si系合金板的表面溫度為470~350℃，且道次所致之Al-Mg-Si系合金板之冷卻、或道次與道次後之強制冷卻所致之平均冷卻速度為50℃/分以上的道次之前項1至前項28中之任1項所記載之Al-Mg-Si系合金板之製造方法。 (29) Among the plurality of passes of hot rolling, the surface temperature of the Al-Mg-Si alloy plate before at least one pass is 470 to 350 ° C, and the Al-Mg-Si system due to the pass The Al-Mg-Si system described in any one of Items 1 to 2 above, which is caused by the cooling of the alloy sheet, or the average cooling rate due to forced cooling after the pass and the pass, is 50 ° C / min or more. A method of manufacturing an alloy sheet.
(30)對含有Si：0.2~0.8質量%、Mg：0.3~1質量%、Fe：0.5質量%以下及Cu：0.5質量%以下，進而含有Ti：0.1質量%以下或B：0.1質量%以下之至少1種，剩餘部分由Al及不可避免的雜質所構成之Al-Mg-Si系合金鑄錠依序實施熱軋、冷軋的合金板之製造方法，其熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為230℃以下，且在熱軋結束後冷軋結束前以200℃以上400℃以下的溫度進行熱處理之Al-Mg-Si系合金板之製造方法。 (30) Containing Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less, and further containing Ti: 0.1% by mass or less or B: 0.1% by mass or less At least one type, the Al-Mg-Si alloy ingot composed of Al and unavoidable impurities is sequentially subjected to hot rolling and cold rolling alloy sheets, and Al- after the hot rolling A method for producing an Al-Mg-Si alloy plate having a surface temperature of 230 ° C or less and a heat treatment at a temperature of 200 ° C to 400 ° C before the end of cold rolling after the completion of hot rolling.
(31)作為雜質之Mn、Cr、及Zn分別規範在0.1質量%以下之前項30所記載之Al-Mg-Si系合金板之製造方法。 (31) Mn, Cr, and Zn, which are impurities, are respectively specified to be 0.1% by mass or less of the method for producing an Al-Mg-Si-based alloy sheet according to Item 30.
(32)作為雜質之Ni、V、Ga、Pb、Sn、Bi及Zr分別規範在0.05質量%以下之前項31所記載之Al-Mg-Si系合金板之製造方法。 (32) Ni, V, Ga, Pb, Sn, Bi, and Zr, which are impurities, are respectively specified to be 0.05% by mass or less of the method for producing an Al-Mg-Si-based alloy sheet according to Item 31.
(33)作為雜質之Ag規範在0.05質量%以下之前項32所記載之Al-Mg-Si系合金板之製造方法。 (33) The method for producing an Al-Mg-Si-based alloy sheet according to Item 32 of 0.05% by mass or less of Ag as an impurity.
(34)作為雜質之稀土類元素之合計含量規範在0.1質量%以下之前項33所記載之Al-Mg-Si系合金板之製造方法。 (34) The total content of the rare earth element as the impurity is 0.1% by mass or less, and the method for producing the Al-Mg-Si alloy plate described in the above item 33.
(35)作為雜質之稀土類元素之合計含量規範在0.1質量%以下之前項34所記載之Al-Mg-Si系合金板之製造方法。 (35) The total content of the rare earth element as the impurity is 0.1% by mass or less, and the method for producing the Al-Mg-Si alloy plate described in the above item 34.
(36)在熱軋結束後冷軋開始前實施熱處理之前項30所記載之Al-Mg-Si系合金板之製造方法。 (36) A method for producing an Al-Mg-Si-based alloy sheet according to Item 30 before the start of the heat treatment before the start of the cold rolling after the completion of the hot rolling.
(37)在熱軋結束後冷軋開始前實施熱處理之前項31所記載之Al-Mg-Si系合金板之製造方法。 (37) A method for producing an Al-Mg-Si-based alloy sheet according to Item 31 before the start of the heat treatment before the start of the cold rolling after the completion of the hot rolling.
(38)在熱軋結束後冷軋開始前實施熱處理之前項32所記載之Al-Mg-Si系合金板之製造方法。 (38) A method for producing an Al-Mg-Si-based alloy sheet according to Item 32 before the start of the heat treatment before the start of the cold rolling after the completion of the hot rolling.
(39)在熱軋結束後冷軋開始前實施熱處理之前項33所記載之Al-Mg-Si系合金板之製造方法。 (39) A method for producing an Al-Mg-Si-based alloy sheet according to Item 33 before heat treatment before the start of cold rolling after completion of hot rolling.
(40)在熱軋結束後冷軋開始前實施熱處理之前項34所記載之Al-Mg-Si系合金板之製造方法。 (40) A method for producing an Al-Mg-Si-based alloy sheet according to Item 34 before the start of the heat treatment before the start of the cold rolling after the completion of the hot rolling.
(41)在熱軋結束後冷軋開始前實施熱處理之前項35所記載之Al-Mg-Si系合金板之製造方法。 (41) A method for producing an Al-Mg-Si-based alloy sheet according to Item 35 before the start of the heat treatment before the start of the cold rolling after the completion of the hot rolling.
(42)熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為200℃以下之前項36所記載之Al-Mg-Si系合金板之製造方法。 (42) A method of producing an Al-Mg-Si-based alloy sheet according to item 36, wherein the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 200 ° C or lower.
(43)熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為200℃以下之前項37所記載之Al-Mg-Si系合金板之製造方法。 (43) A method for producing an Al-Mg-Si-based alloy sheet according to Item 37, wherein the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 200 ° C or lower.
(44)熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為200℃以下之前項38所記載之Al-Mg-Si系合金板之製造方法。 (44) A method for producing an Al-Mg-Si-based alloy sheet according to item 38, wherein the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 200 ° C or lower.
(45)熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為200℃以下之前項39所記載之Al-Mg-Si系合金板之製造方法。 (45) The surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 200 ° C or lower, and the method for producing the Al-Mg-Si-based alloy sheet described in the above item 39.
(46)熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為200℃以下之前項40所記載之Al-Mg-Si系合金板之製造方法。 (46) A method for producing an Al-Mg-Si-based alloy sheet according to item 40, wherein the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 200 ° C or lower.
(47)熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為200℃以下之前項41所記載之Al-Mg-Si系合金板之製造方法。 (47) The surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 200 ° C or lower, and the method for producing the Al-Mg-Si-based alloy sheet described in the above item 41.
(48)熱處理溫度為200℃以上300℃以下之前項42所記載之Al-Mg-Si系合金板之製造方法。 (48) A method for producing an Al-Mg-Si-based alloy sheet according to item 42 of the heat treatment temperature of 200 ° C or more and 300 ° C or less.
(49)熱處理溫度為200℃以上300℃以下之前項43所記載之Al-Mg-Si系合金板之製造方法。 (49) A method for producing an Al-Mg-Si-based alloy sheet according to item 43 of the heat treatment temperature of 200 ° C or more and 300 ° C or less.
(50)熱處理溫度為200℃以上300℃以下之前項44所記載之Al-Mg-Si系合金板之製造方法。 (50) A method for producing an Al-Mg-Si-based alloy sheet according to item 44 of the heat treatment temperature of 200 ° C or more and 300 ° C or less.
(51)熱處理溫度為200℃以上300℃以下之前項45所記載之Al-Mg-Si系合金板之製造方法。 (51) A method for producing an Al-Mg-Si-based alloy sheet according to Item 45, wherein the heat treatment temperature is 200 ° C or more and 300 ° C or less.
(52)熱處理溫度為200℃以上300℃以下之前項46所記載之Al-Mg-Si系合金板之製造方法。 (52) A method for producing an Al-Mg-Si-based alloy sheet according to item 46, wherein the heat treatment temperature is 200 ° C or more and 300 ° C or less.
(53)熱處理溫度為200℃以上300℃以下之前項47所記載之Al-Mg-Si系合金板之製造方法。 (53) A method for producing an Al-Mg-Si-based alloy sheet according to item 47, wherein the heat treatment temperature is 200 ° C or more and 300 ° C or less.
(54)熱處理後之冷軋之壓延率為20%以上之前項48所記載之Al-Mg-Si系合金板之製造方法。 (54) A method of producing an Al-Mg-Si-based alloy sheet according to item 48, wherein the rolling ratio of the cold rolling after the heat treatment is 20% or more.
(55)熱處理後之冷軋之壓延率為20%以上之前項49所記載之Al-Mg-Si系合金板之製造方法。 (55) A method of producing an Al-Mg-Si-based alloy sheet according to Item 49, wherein the rolling ratio of the cold rolling after the heat treatment is 20% or more.
(56)熱處理後之冷軋之壓延率為20%以上之前項50所記載之Al-Mg-Si系合金板之製造方法。 (56) A method of producing an Al-Mg-Si-based alloy sheet according to item 50, wherein the rolling ratio of the cold rolling after the heat treatment is 20% or more.
(57)熱處理後之冷軋之壓延率為20%以上之前項51所記載之Al-Mg-Si系合金板之製造方法。 (57) A method of producing an Al-Mg-Si-based alloy sheet according to Item 51, wherein the rolling ratio of the cold rolling after the heat treatment is 20% or more.
(58)熱處理後之冷軋之壓延率為20%以上之前項52所記載之Al-Mg-Si系合金板之製造方法。 (58) A method of producing an Al-Mg-Si-based alloy sheet according to Item 52, wherein the rolling ratio of the cold rolling after the heat treatment is 20% or more.
(59)熱處理後之冷軋之壓延率為20%以上之前項53所記載之Al-Mg-Si系合金板之製造方法。 (59) A method of producing an Al-Mg-Si-based alloy sheet according to Item 53 of the present invention, wherein the rolling ratio of the cold rolling after the heat treatment is 20% or more.
(60)冷軋後實施最終退火之前項54所記載之Al-Mg-Si系合金板之製造方法。 (60) A method for producing an Al-Mg-Si-based alloy sheet according to Item 54 before final annealing after cold rolling.
(61)冷軋後實施最終退火之前項55所記載之Al-Mg-Si系合金板之製造方法。 (61) A method for producing an Al-Mg-Si-based alloy sheet according to Item 55 before final annealing after cold rolling.
(62)冷軋後實施最終退火之前項56所記載之Al-Mg-Si系合金板之製造方法。 (62) A method for producing an Al-Mg-Si-based alloy sheet according to Item 56 before final annealing after cold rolling.
(63)冷軋後實施最終退火之前項57所記載之Al-Mg-Si系合金板之製造方法。 (63) A method for producing an Al-Mg-Si-based alloy sheet according to Item 57 before final annealing after cold rolling.
(64)冷軋後實施最終退火之前項58所記載之Al-Mg-Si系合金板之製造方法。 (64) A method for producing an Al-Mg-Si-based alloy sheet according to Item 58 before final annealing after cold rolling.
(65)冷軋後實施最終退火之前項59所記載之Al-Mg-Si系合金板之製造方法。 (65) A method for producing an Al-Mg-Si-based alloy sheet according to Item 59 before final annealing after cold rolling.
(66)最終退火之溫度為200℃以下之前項60所記載之Al-Mg-Si系合金板之製造方法。 (66) The method of producing the Al-Mg-Si alloy sheet according to the above item 60, wherein the temperature of the final annealing is 200 ° C or lower.
(67)最終退火之溫度為200℃以下之前項61所記載之Al-Mg-Si系合金板之製造方法。 (67) The method of producing the Al-Mg-Si-based alloy sheet described in the above item 61 at a temperature at which the final annealing is 200 ° C or lower.
(68)最終退火之溫度為200℃以下之前項62所記載之Al-Mg-Si系合金板之製造方法。 (68) The final annealing temperature is 200 ° C or lower, and the method for producing the Al-Mg-Si alloy sheet described in the above item 62.
(69)最終退火之溫度為200℃以下之前項63所記載之Al-Mg-Si系合金板之製造方法。 (69) The method of producing the Al-Mg-Si-based alloy sheet described in the above item 63, wherein the temperature of the final annealing is 200 ° C or lower.
(70)最終退火之溫度為200℃以下之前項64所記載之Al-Mg-Si系合金板之製造方法。 (70) The method of producing the Al-Mg-Si alloy sheet according to the above item 64, wherein the temperature of the final annealing is 200 ° C or lower.
(71)最終退火之溫度為200℃以下之前項65所記載之Al-Mg-Si系合金板之製造方法。 (71) The method of producing the Al-Mg-Si-based alloy sheet described in the above item 65, wherein the temperature of the final annealing is 200 ° C or lower.
(72)在熱軋之複數道次之中，至少實施1次道次前之Al-Mg-Si系合金板的表面溫度為470~350℃，且道次所致之Al-Mg-Si系合金板之冷卻、或道次與道次後之強制冷卻所致之平均冷卻速度為50℃/分以上的道次之前項30 至前項71中之任1項所記載之Al-Mg-Si系合金板之製造方法。 (72) Among the plurality of passes of hot rolling, the surface temperature of the Al-Mg-Si alloy plate before at least one pass is 470 to 350 ° C, and the Al-Mg-Si system due to the pass The cooling of the alloy plate, or the average cooling rate caused by the forced cooling after the pass and the pass is 50 ° C / min or more. The method for producing an Al-Mg-Si-based alloy sheet according to any one of the preceding items.
依據前項(1)所記載之發明，由於對Al-Mg-Si系合金鑄錠依序實施熱軋、冷軋的合金板之製造方法，其熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為230℃以下，且在熱軋結束後冷軋結束前以200℃以上400℃以下的溫度進行熱處理，故可得到熱軋所致之有效的淬火效果，熱處理時使導電率更提升，藉由其後之冷軋使其加工硬化，藉此可製造拉伸強度及導電率顯示高值之加工性良好的Al-Mg-Si系合金板。 According to the invention described in the above (1), the Al-Mg-Si alloy after the hot rolling is just after the method of manufacturing the hot-rolled and cold-rolled alloy sheet in the Al-Mg-Si alloy ingot. The surface temperature of the sheet is 230 ° C or less, and heat treatment is performed at a temperature of 200 ° C or more and 400 ° C or less before the end of cold rolling after hot rolling, so that an effective quenching effect by hot rolling can be obtained, and conductivity is further improved by heat treatment. The aluminum-based Mg-Si alloy sheet having excellent tensile strength and high electrical conductivity and high workability can be produced by work-hardening by cold rolling thereafter.
依據前項(2)所記載之發明，由於Al-Mg-Si系合金鑄錠之化學組成係含有Si：0.2~0.8質量%、Mg：0.3~1質量%、Fe：0.5質量%以下及Cu：0.5質量%以下，剩餘部分由Al及不可避免的雜質所構成，故可製造拉伸強度及導電率顯示高值之加工性良好的Al-Mg-Si系合金板。 According to the invention described in the above (2), the chemical composition of the Al-Mg-Si alloy ingot contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: When the amount is 0.5% by mass or less and the remainder is composed of Al and unavoidable impurities, an Al-Mg-Si-based alloy sheet having excellent workability in tensile strength and high electrical conductivity can be produced.
依據前項(3)及(4)所記載之發明，由於作為雜質之Mn、Cr、Zn、及Ti分別規範在0.1質量%以下，故可製造拉伸強度及導電率顯示高值之加工性良好的Al-Mg-Si系合金板。 According to the inventions of the above-mentioned items (3) and (4), since Mn, Cr, Zn, and Ti, which are impurities, are respectively specified to be 0.1% by mass or less, workability in which tensile strength and electrical conductivity exhibit high values can be produced. Al-Mg-Si alloy plate.
依據前項(5)~(8)所記載之發明，由於在熱軋結束後冷軋開始前實施熱處理，故藉由其後之冷軋使其加工硬化可製造拉伸強度及導電率顯示高值之加工性良好的 Al-Mg-Si系合金板。 According to the invention of the above (5) to (8), since the heat treatment is performed before the start of the cold rolling after the completion of the hot rolling, the workability and the subsequent cold rolling are used to produce a tensile strength and a high conductivity. Good processability Al-Mg-Si alloy plate.
依據前項(9)~(12)所記載之發明，由於熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為200℃以下，故可提高熱軋所致之淬火效果。 According to the invention of the above (9) to (12), since the surface temperature of the Al-Mg-Si alloy plate immediately after the hot rolling is 200 ° C or lower, the quenching effect by hot rolling can be improved.
依據前項(13)~(16)所記載之發明，由於熱處理溫度為200℃以上300℃以下，故可確實地使導電率與強度提升。 According to the invention of the above (13) to (16), since the heat treatment temperature is 200 ° C or more and 300 ° C or less, the electrical conductivity and strength can be surely improved.
依據前項(17)~(20)所記載之發明，由於熱處理後之冷軋之壓延率為20%以上，故藉由冷軋使Al-Mg-Si系合金板強度提升的同時可得到良好的加工性。 According to the invention of the above (17) to (20), since the rolling ratio of the cold rolling after the heat treatment is 20% or more, the strength of the Al-Mg-Si alloy sheet is improved by cold rolling, and good results are obtained. Processability.
依據前項(21)~(24)所記載之發明，由於冷軋後實施最終退火，故成為Al-Mg-Si系合金板之加工性良好者。 According to the invention of the above (21) to (24), since the final annealing is performed after the cold rolling, the Al-Mg-Si alloy plate is excellent in workability.
依據前項(25)~(28)所記載之發明，由於最終退火之溫度為200℃以下，故可製造拉伸強度及導電率顯示高值之加工性良好的Al-Mg-Si系合金板。 According to the invention of the above-mentioned items (25) to (28), since the temperature of the final annealing is 200 ° C or lower, an Al—Mg—Si-based alloy sheet having excellent tensile properties and high electrical conductivity and high workability can be produced.
依據前項(29)所記載之發明，由於在熱軋之複數道次之中，至少實施1次道次前之Al-Mg-Si系合金板的表面溫度為470~350℃，且道次所致之Al-Mg-Si系合金板之冷卻、或道次與道次後之強制冷卻所致之平均冷卻速度為50℃/分以上的道次，故可提高熱軋所致之淬火效果。 According to the invention of the above item (29), the surface temperature of the Al-Mg-Si alloy plate before the pass of at least one pass in the plurality of passes of the hot rolling is 470 to 350 ° C, and the pass The cooling rate of the Al-Mg-Si alloy plate, or the average cooling rate caused by forced cooling after the pass and the pass is 50 ° C / min or more, so that the quenching effect by hot rolling can be improved.
依據前項(30)所記載之發明，由於對含有Si：0.2~0.8質量%、Mg：0.3~1質量%、Fe：0.5質量%以下及Cu：0.5質量%以下，進而含有Ti：0.1質量%以下或B： 0.1質量%以下之至少1種，剩餘部分由Al及不可避免的雜質所構成之Al-Mg-Si系合金鑄錠依序實施熱軋、冷軋的合金板之製造方法，熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為230℃以下，且在熱軋結束後冷軋結束前以200℃以上且未達400℃的溫度進行熱處理，故可得到熱軋所致之有效的淬火效果，熱處理時使導電率更提升，藉由其後之冷軋使其加工硬化，藉此可製造拉伸強度及導電率顯示高值之加工性良好的Al-Mg-Si系合金板。 According to the invention of the above (30), the content of Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less, and further Ti: 0.1% by mass. Following or B: At least one of 0.1% by mass or less, and the Al-Mg-Si alloy ingot composed of Al and unavoidable impurities is sequentially subjected to hot rolling and cold rolling of an alloy sheet, and immediately after the hot rolling The surface temperature of the Al-Mg-Si alloy plate is 230 ° C or less, and heat treatment is performed at a temperature of 200 ° C or more and less than 400 ° C before the end of cold rolling after hot rolling, so that hot rolling can be obtained. The quenching effect improves the electrical conductivity during heat treatment and is work hardened by cold rolling thereafter, thereby producing an Al-Mg-Si alloy sheet having excellent workability in which tensile strength and electrical conductivity show high values. .
依據前項(31)所記載之發明，由於作為雜質之Mn、Cr、及Zn分別規範在0.1質量%以下，故可製造拉伸強度及導電率顯示高值之加工性良好的Al-Mg-Si系合金板。 According to the invention of the above (31), since Mn, Cr, and Zn, which are impurities, are respectively specified to be 0.1% by mass or less, Al-Mg-Si having excellent workability in which tensile strength and electrical conductivity show high values can be produced. Alloy plate.
依據前項(32)所記載之發明，由於作為雜質之Ni、V、Ga、Pb、Sn、Bi及Zr分別規範在0.05質量%以下，故可製造拉伸強度及導電率顯示高值之加工性良好的Al-Mg-Si系合金板。 According to the invention of the above (32), since Ni, V, Ga, Pb, Sn, Bi, and Zr, which are impurities, are respectively specified to be 0.05% by mass or less, workability in which tensile strength and electrical conductivity exhibit high values can be produced. Good Al-Mg-Si alloy sheet.
依據前項(33)所記載之發明，由於作為雜質之Ag規範在0.05質量%以下，故可製造拉伸強度及導電率顯示高值之加工性良好的Al-Mg-Si系合金板。 According to the invention of the above (33), since the Ag specification as the impurity is 0.05% by mass or less, an Al-Mg-Si-based alloy sheet having excellent tensile properties and high electrical conductivity and high workability can be produced.
依據前項(34)及(35)所記載之發明，由於作為雜質之稀土類元素之合計含量規範在0.1質量%以下，故可製造拉伸強度及導電率顯示高值之加工性良好的Al-Mg-Si系合金板。 According to the invention of the above-mentioned items (34) and (35), since the total content of the rare earth elements as the impurities is 0.1% by mass or less, it is possible to produce Al-having excellent workability in which the tensile strength and the electrical conductivity show high values. Mg-Si alloy plate.
依據前項(36)~(41)所記載之發明，由於在熱軋 結束後冷軋開始前實施熱處理，故藉由其後之冷軋使其加工硬化，藉此可製造拉伸強度及導電率顯示高值之加工性良好的Al-Mg-Si系合金板。 According to the invention described in the above items (36) to (41), due to hot rolling After the completion of the cold rolling before the end of the cold rolling, the heat treatment is performed by cold rolling, whereby an Al-Mg-Si alloy sheet having excellent workability in tensile strength and high electrical conductivity can be produced.
依據前項(42)~(47)所記載之發明，由於熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為200℃以下，故可提高熱軋所致之淬火效果。 According to the invention of the above (42) to (47), since the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 200 ° C or lower, the quenching effect by hot rolling can be improved.
依據前項(48)~(53)所記載之發明，由於熱處理溫度為200℃以上300℃以下，故可確實地使導電率與強度提升。 According to the invention of the above (48) to (53), since the heat treatment temperature is 200 ° C or more and 300 ° C or less, the electrical conductivity and strength can be surely improved.
前項(54)~(59)所記載之發明，由於熱處理後之冷軋之壓延率為20%以上，故藉由冷軋使Al-Mg-Si系合金板強度提升的同時可得到良好的加工性。 In the invention according to the above paragraphs (54) to (59), since the rolling ratio of the cold rolling after the heat treatment is 20% or more, the strength of the Al-Mg-Si alloy sheet is improved by cold rolling, and good processing can be obtained. Sex.
依據前項(60)~(65)所記載之發明，由於冷軋後實施最終退火，故成為Al-Mg-Si系合金板之加工性良好者。 According to the invention of the above (60) to (65), since the final annealing is performed after the cold rolling, the Al-Mg-Si alloy sheet is excellent in workability.
依據前項(66)~(71)所記載之發明，由於最終退火之溫度為200℃以下，故可製造拉伸強度及導電率顯示高值之加工性良好的Al-Mg-Si系合金板。 According to the invention of the above-mentioned (66) to (71), since the temperature of the final annealing is 200 ° C or lower, an Al—Mg—Si-based alloy sheet having excellent tensile properties and high electrical conductivity and high workability can be produced.
依據前項(72)所記載之發明，由於在熱軋之複數道次之中，至少實施1次道次前之Al-Mg-Si系合金板的表面溫度為470~350℃，且道次所致之Al-Mg-Si系合金板之冷卻、或道次與道次後之強制冷卻所致之平均冷卻速度為50℃/分以上的道次，故可提高熱軋所致之淬火效果。 According to the invention of the above (72), the surface temperature of the Al-Mg-Si alloy plate before the pass of at least one pass in the plurality of passes of the hot rolling is 470 to 350 ° C, and the pass The cooling rate of the Al-Mg-Si alloy plate, or the average cooling rate caused by forced cooling after the pass and the pass is 50 ° C / min or more, so that the quenching effect by hot rolling can be improved.
本案發明者發現藉由在依序實施熱軋、冷軋的Al-Mg-Si系合金板之製造方法中，使熱軋完之合金板的表面溫度成為指定的溫度以下，並施以在熱軋結束後冷軋結束前熱處理，可得到具有高導電率與良好的加工性同時具有高強度之Al-Mg-Si系合金板，終至完成本案發明。 The inventors of the present invention have found that in the method for producing an Al-Mg-Si alloy plate which is sequentially subjected to hot rolling and cold rolling, the surface temperature of the hot rolled alloy sheet is equal to or lower than a predetermined temperature, and is applied to heat. After the end of the cold rolling, the heat treatment before the end of the cold rolling can obtain an Al-Mg-Si alloy plate having high electrical conductivity and good workability while having high strength, and the invention of the present invention is completed.
以下，詳細說明關於本案之Al-Mg-Si系合金板之製造方法。 Hereinafter, a method of producing the Al-Mg-Si-based alloy sheet according to the present invention will be described in detail.
本案之Al-Mg-Si系合金組成中，顯示各元素之添加目的及較佳含量。 In the Al-Mg-Si alloy composition of the present invention, the purpose of addition and the preferred content of each element are shown.
Mg及Si為強度表現所必須的元素，各自的含量為Si：0.2質量%以上0.8質量%以下、Mg：0.3質量%以上1質量%以下較佳。Si含量未達0.2質量%或Mg含量未達0.3質量%時強度變低。另一方面，若Si含量超過0.8質量%、Mg含量超過1質量%時，熱軋時的壓延負荷變高而生產性降低，所得之鋁合金板的成形加工性亦變差。Si含量為0.2質量%以上0.6質量%以下更佳，進而0.32質量%以上0.60質量%以下特佳。Mg含量為0.4質量%以上1.0質量%以下更佳，0.45質量%以上0.9質量%以下更佳，特別是0.45質量%以上0.55質量%以下較佳。 Mg and Si are elements necessary for strength expression, and each content is Si: 0.2% by mass or more and 0.8% by mass or less, and Mg: 0.3% by mass or more and 1% by mass or less. When the Si content is less than 0.2% by mass or the Mg content is less than 0.3% by mass, the strength becomes low. On the other hand, when the Si content is more than 0.8% by mass and the Mg content is more than 1% by mass, the rolling load during hot rolling is increased, and the productivity is lowered, and the formability of the obtained aluminum alloy sheet is also deteriorated. The Si content is preferably 0.2% by mass or more and 0.6% by mass or less, more preferably 0.32% by mass or more and 0.60% by mass or less. The Mg content is preferably 0.4% by mass or more and 1.0% by mass or less, more preferably 0.45 mass% or more and 0.9 mass% or less, and particularly preferably 0.45 mass% or more and 0.55 mass% or less.
雖Fe及Cu為成形加工上必要之成分，但若大量含有則耐蝕性降低。本案中Fe含量及Cu含量分別規範在0.5質量%以下較佳。Fe含量規範在0.35質量%以下更佳，特別是0.1質量%以上0.25質量%以下較佳。Cu含量為0.2 質量%以下更佳，特別是0.1質量%以下較佳。 Although Fe and Cu are components necessary for the forming process, if they are contained in a large amount, the corrosion resistance is lowered. In the present case, the Fe content and the Cu content are preferably 0.5% by mass or less, respectively. The Fe content specification is more preferably 0.35 mass% or less, particularly preferably 0.1 mass% or more and 0.25 mass% or less. Cu content is 0.2 The mass% or less is more preferably, and particularly preferably 0.1% by mass or less.
又，合金元素中雖含有各種不可避免的雜質元素，但由於Mn及Cr會使傳導性及導電性降低，Zn含量變多時會使合金材的耐腐蝕性降低故以少量較佳。Ti有防止合金在鑄造成鋼胚時發生結晶粒微細化並凝固裂開的效果，但由於大量含有時則結晶物會生成很多尺寸大的結晶物，製品的加工性或熱傳導性及導電率降低。作為雜質之Mn、Cr、Zn及Ti之各自的含量為0.1質量%以下較佳，進而0.05質量%以下較佳。 Further, although the alloy element contains various unavoidable impurity elements, Mn and Cr lower the conductivity and conductivity, and when the Zn content is increased, the corrosion resistance of the alloy material is lowered, so that a small amount is preferable. Ti has an effect of preventing the crystal grains from being fined and solidified when the alloy is cast into a steel embryo. However, when a large amount is contained, the crystals generate a large number of crystals having a large size, and the processability or thermal conductivity and electrical conductivity of the product are lowered. . The content of each of Mn, Cr, Zn, and Ti as impurities is preferably 0.1% by mass or less, more preferably 0.05% by mass or less.
Ti及B有防止合金在鑄造成鋼胚時發生結晶粒微細化並凝固裂開的效果。前述效果可藉由添加Ti或B之至少1種而得，添加兩者亦可。然而，由於大量含有時則結晶物會生成很多尺寸大的結晶物，製品的加工性或熱傳導性及導電率降低。Ti含量為0.1質量以下較佳，進而0.005質量%以上0.05質量%以下較佳。又，B含量為0.1質量%以下較佳，特別是0.06質量%較佳。 Ti and B have an effect of preventing crystal grain refinement and solidification cracking when the alloy is cast into a steel preform. The above effects can be obtained by adding at least one of Ti or B, and both may be added. However, when a large amount is contained, crystals are formed into many large-sized crystals, and the processability or thermal conductivity and electrical conductivity of the product are lowered. The Ti content is preferably 0.1% by mass or less, more preferably 0.005% by mass or more and 0.05% by mass or less. Further, the B content is preferably 0.1% by mass or less, particularly preferably 0.06% by mass.
作為上述以外之其他雜質元素，雖可舉例Ni、V、Ga、Pb、Sn、Bi、Zr、Ag、稀土類等，但不限定於此等，此等其他雜質元素之中除了稀土類以外各個元素之含量為0.05質量%以下較佳。上述其他雜質元素之中的稀土類，雖可包含1種或複數種元素，亦可為源自以美鈰合金狀態包含的鑄造用原料者，但稀土類元素之合計含量為0.1質量%以下較佳，進而0.05質量%以下較佳。 Examples of other impurity elements other than the above include Ni, V, Ga, Pb, Sn, Bi, Zr, Ag, and rare earths. However, the present invention is not limited thereto, and among these other impurity elements, each of the rare earth elements The content of the element is preferably 0.05% by mass or less. The rare earth element among the above-mentioned other impurity elements may be one or a plurality of elements, and may be a raw material for casting which is contained in the state of the alloy, but the total content of the rare earth elements is 0.1% by mass or less. Preferably, it is preferably 0.05% by mass or less.
接著，記述關於用以得到本案規定之Al-Mg-Si系合 金板的處理步驟。 Next, describe the Al-Mg-Si system used to obtain the provisions of this case. Gold plate processing steps.
使用常法進行溶解成分調整，得到Al-Mg-Si系合金鑄錠。對所得之合金鑄錠藉由熱軋前加熱實施均質化處理作為前步驟較佳。 The dissolved component was adjusted by a usual method to obtain an Al-Mg-Si alloy ingot. It is preferred that the obtained alloy ingot is subjected to homogenization treatment by heating before hot rolling as a pre-step.
前述均質化處理以500℃以上進行較佳。 The above homogenization treatment is preferably carried out at 500 ° C or higher.
前述熱軋前加熱雖是為了在Al-Mg-Si系合金鑄錠中使結晶物及Mg、Si固溶成為均勻的組織而實施，但由於溫度若過高則鑄錠中有發生部分融解的可能性，以450℃以上580℃以下進行較佳，特別是以500℃以上580℃以下進行較佳。 The pre-hot rolling is performed to solidify the crystal and the Mg and Si into a uniform structure in the Al-Mg-Si alloy ingot. However, if the temperature is too high, partial melting occurs in the ingot. The possibility is preferably 450 ° C or more and 580 ° C or less, and more preferably 500 ° C or more and 580 ° C or less.
對Al-Mg-Si系合金鑄錠進行均質化處理後進行冷卻，可進行熱軋前加熱，亦可連續進行均質化處理與熱軋前加熱，在前述均質化處理及熱軋前加熱之較佳溫度範圍內以兼顧均質化處理與熱軋前加熱的相同溫度進行加熱亦可。 The Al-Mg-Si alloy ingot is homogenized and then cooled, and can be heated before hot rolling, or continuously subjected to homogenization treatment and heating before hot rolling, and the above homogenization treatment and heating before hot rolling In the preferred temperature range, heating may be performed at the same temperature as that of the homogenization treatment and the pre-hot rolling.
為了去除鑄造後熱軋前加熱前鑄錠之表面附近的雜質層，對鑄錠施以面削較佳。面削可在鑄造後均質化處理前，亦可在均質化處理後熱軋前加熱前。 In order to remove the impurity layer near the surface of the ingot before heating after hot rolling after casting, it is preferable to apply the face to the ingot. The face cutting may be performed before the homogenization treatment after casting, or before the heating after the homogenization treatment.
對熱軋前加熱後之Al-Mg-Si系合金鑄錠施以熱軋。 The Al-Mg-Si alloy ingot heated before the hot rolling is subjected to hot rolling.
熱軋係由粗熱軋與終熱軋組成，使用粗熱軋機進行由複數道次而成之粗熱軋後，使用與粗熱軋機不同的終熱軋機進行終熱軋。此外，本案中，將以粗熱軋機之最終道次作為熱軋之最終道次時，可省略終熱軋。 The hot rolling is composed of rough hot rolling and final hot rolling, and after rough hot rolling by a plurality of passes using a rough hot rolling mill, final hot rolling is performed using a final hot rolling mill different from the rough hot rolling mill. Further, in the present case, when the final pass of the rough hot rolling mill is taken as the final pass of the hot rolling, the final hot rolling can be omitted.
本案中，終熱軋使用連續設置有上下一組之工作軋輥 或二組以上之工作軋輥的壓延機，從1個方向導入Al-Mg-Si系合金板並以1次道次實施。 In this case, the final hot rolling uses a work roll that is continuously provided with the upper and lower groups. Or a calender of two or more sets of work rolls, which is introduced into the Al-Mg-Si alloy plate from one direction and is carried out in one pass.
以鋼捲實施冷軋時，可以捲取裝置捲取終熱軋後之Al-Mg-Si系合金板做成熱軋鋼捲。省略終熱軋，將粗熱軋之最終道次作為熱軋之最終道次時，粗熱軋之後，可利用捲取裝置捲取Al-Mg-Si系合金板做成熱軋鋼捲。 When the steel coil is subjected to cold rolling, the Al-Mg-Si alloy sheet after the final hot rolling can be wound up by the winding device to form a hot rolled steel coil. When the final hot rolling is omitted and the final pass of the rough hot rolling is taken as the final pass of the hot rolling, after the rough hot rolling, the Al-Mg-Si alloy plate can be wound up by a winding device to form a hot rolled steel coil.
粗熱軋中，依循溶體化處理Mg及Si保持在固溶之狀態後，藉由粗熱軋之道次所致之Al-Mg-Si系合金板的冷卻，或粗熱軋之道次後與道次後的強制冷卻所致之溫度降低而可得到淬火之效果。 In the rough hot rolling, after the solution treatment of Mg and Si is maintained in a solid solution state, the cooling of the Al-Mg-Si alloy plate by the rough hot rolling pass, or the rough hot rolling pass The effect of quenching can be obtained by lowering the temperature caused by forced cooling after the pass.
本案中將在粗熱軋之複數道次之中，道次前之Al-Mg-Si系合金板的表面溫度為350℃以上470℃以下，且道次所致之Al-Mg-Si系合金板的冷卻、或道次與道次後之強制冷卻之平均冷卻速度為50℃/分以上的道次稱為控制道次。使控制道次前之Al-Mg-Si系合金板之表面溫度成為350℃以上470℃以下，是因為未達350℃時粗熱軋中之急冷所致之淬火的效果小，較470℃高的溫度時道次完之Al-Mg-Si系合金板的急冷為困難的原因。 In the present case, among the plurality of passes of the rough hot rolling, the surface temperature of the Al-Mg-Si alloy plate before the pass is 350 ° C or more and 470 ° C or less, and the Al-Mg-Si alloy is caused by the pass. The pass of the plate cooling, or the average cooling rate of the forced cooling after the pass and the pass after the pass is 50 ° C / min or more is called the control pass. The surface temperature of the Al-Mg-Si alloy plate before the control pass is 350° C. or higher and 470° C. or lower, because the quenching effect due to quenching in the rough hot rolling at 350° C. is small, and is higher than 470° C. The quenching of the Al-Mg-Si alloy plate after the completion of the temperature is a cause of difficulty.
上述平均冷卻速度係定為在控制道次中不進行強制冷卻時為自控制道次開始至結束為止，控制道次後進行強制冷卻時為自控制道次開始至強制冷卻結束為止之Al-Mg-Si系合金板的降低溫度(℃)除以所需時間(分)之值。 The average cooling rate is set to be Al-Mg from the start of the control pass to the end of the control pass when the forced flow is not performed in the control pass, and from the start of the control pass to the end of the forced cooling when the forced cooling is performed after the control pass. The reduced temperature (°C) of the -Si alloy plate is divided by the value of the desired time (minutes).
控制道次後的強制冷卻可一邊壓延Al-Mg-Si系合金板一邊對壓延後之部位依序實施，亦可壓延Al-Mg-Si系 合金板全體後實施。強制冷卻的方法雖未限定，但可用水冷亦可用氣冷，亦可利用冷卻劑。 The forced cooling after the control of the pass can be performed by rolling the Al-Mg-Si alloy plate while pressing the rolled portion, or rolling the Al-Mg-Si system. The entire alloy plate is implemented. Although the method of forced cooling is not limited, it may be water-cooled or air-cooled, or a coolant may be used.
前述控制道次實施至少1次較佳，實施複數次亦可。實施複數次控制道次時，對於各個控制道次可選擇道次後是否進行強制冷卻。雖只要是道次前之Al-Mg-Si系合金板的表面溫度為470~350℃且冷卻速度為50℃/分以上的話控制道次便可實施複數次，但可藉由以1次的控制道次使Al-Mg-Si系合金板的溫度降低至未達350℃而效率佳且有效地進行淬火。 It is preferable that the control channel is implemented at least once, and it may be performed plural times. When multiple control passes are performed, whether forced cooling is performed after the pass can be selected for each control pass. Although the surface temperature of the Al-Mg-Si alloy plate before the pass is 470 to 350 ° C and the cooling rate is 50 ° C / min or more, the control pass can be performed plural times, but by one time The control pass reduces the temperature of the Al-Mg-Si alloy plate to less than 350 ° C and is efficient and effective for quenching.
本案中，粗熱軋之最終道次後未進行強制冷卻時，將熱軋之最終道次剛完成後之Al-Mg-Si系合金板的表面溫度定為粗熱軋完溫度，粗熱軋之最終道次後進行強制冷卻時，將強制冷卻剛結束後之Al-Mg-Si系合金板的表面溫度定為粗熱軋完溫度。 In the present case, when the forced cooling is not performed after the final pass of the rough hot rolling, the surface temperature of the Al-Mg-Si alloy plate after the final pass of the hot rolling is determined as the rough hot rolling temperature, and the rough hot rolling is performed. When forced cooling is performed after the final pass, the surface temperature of the Al-Mg-Si alloy plate immediately after the forced cooling is set to the rough hot rolling temperature.
本案中實施終熱軋時以終熱軋的結束，未實施終熱軋時以粗熱軋之最終道次的結束作為熱軋的結束，使熱軋剛結束後之Al-Mg-Si系合金板的表面溫度成為230℃以下。藉由使熱軋剛結束後之合金板之溫度成為230℃以下可得到有效之淬火效果。 In the present case, the final hot rolling is performed at the end of the final hot rolling, and the end of the final pass of the rough hot rolling is not performed as the end of the hot rolling, and the Al-Mg-Si alloy immediately after the hot rolling is finished. The surface temperature of the board is 230 ° C or less. An effective quenching effect can be obtained by setting the temperature of the alloy sheet immediately after the completion of hot rolling to 230 ° C or lower.
熱軋剛結束後之Al-Mg-Si系合金板的表面溫度若過高，淬火的效果不足，即使熱軋結束後冷軋結束前實施熱處理強度的提升亦不充分。熱軋剛結束後之Al-Mg-Si系合金板的表面溫度為200℃以下較佳，進一步為150℃以下較佳，特別是130℃以下較佳。 If the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is too high, the effect of quenching is insufficient, and the improvement of the heat treatment strength before the end of the cold rolling after the completion of the hot rolling is insufficient. The surface temperature of the Al-Mg-Si alloy plate immediately after the hot rolling is preferably 200 ° C or lower, more preferably 150 ° C or lower, and particularly preferably 130 ° C or lower.
此外，粗熱軋之後進行終熱軋時，為了得到終熱軋之道次所致之淬火效果，終熱軋前之Al-Mg-Si系合金板的表面溫度為270℃以下較佳。 Further, in the case of final hot rolling after rough hot rolling, in order to obtain the quenching effect by the finish hot rolling, the surface temperature of the Al-Mg-Si alloy plate before the final hot rolling is preferably 270 ° C or lower.
又，不進行終熱軋且粗熱軋之最終道次並非控制道次時亦同樣地，粗熱軋最終道次前之Al-Mg-Si系合金板的表面溫度為270℃以下較佳。 Further, in the case where the final hot rolling is not performed and the final pass of the rough hot rolling is not the control pass, the surface temperature of the Al-Mg-Si alloy plate before the final pass of the rough hot rolling is preferably 270 ° C or lower.
另一方面，不進行終熱軋且粗熱軋之最終道次為控制道次時，由於控制道次成為熱軋之最終道次，故以熱軋之最終道次前之Al-Mg-Si系合金板的表面溫度為470~350℃，且藉由壓延或壓延與壓延後之強制冷卻而以冷卻速度為50℃/分以上之冷卻速度合金板的表面溫度成為230℃以下之方式實施控制道次。 On the other hand, when the final pass is not subjected to the final hot rolling and the final pass of the rough hot rolling is the control pass, since the control pass becomes the final pass of the hot rolling, the Al-Mg-Si before the final pass of the hot rolling is used. The surface temperature of the alloy plate is 470 to 350 ° C, and the surface temperature of the alloy plate is controlled to be 230 ° C or less at a cooling rate of 50 ° C / min or more by calendering or rolling and forced cooling after rolling. Pass.
對於熱軋結束後冷軋結束前之Al-Mg-Si系合金板，在使Mg2Si微細且均勻地析出，並且使Al-Mg-Si系合金板中存在之加工變形減少的目的下實施熱處理。 The Al-Mg-Si alloy sheet before the end of the cold rolling after the completion of the hot rolling is carried out under the purpose of finely and uniformly depositing Mg 2 Si and reducing the processing distortion existing in the Al—Mg—Si-based alloy sheet. Heat treatment.
本案中熱軋結束後冷軋結束前之對Al-Mg-Si系合金板的熱處理為了得到導電率提升的效果以200℃以上400℃以下的溫度實施。熱處理溫度未達200℃時導電率提升有界限，熱處理溫度若超過400℃，則不能得到形成了粗大析出物之最終製品的高強度或良好的成形加工性。進而若成為450℃以上則因再結晶粒的粗大化而對最終製品之成形加工性有壞影響。前述熱處理的溫度為200℃以上300℃以下較佳，進一步為210℃以上280℃以下較佳。 In the present invention, the heat treatment for the Al-Mg-Si alloy plate before the end of the cold rolling after the completion of the cold rolling is performed at a temperature of 200 ° C or more and 400 ° C or less in order to obtain an effect of improving the conductivity. When the heat treatment temperature is less than 200 ° C, the conductivity is increased. If the heat treatment temperature exceeds 400 ° C, high strength or good moldability of the final product in which coarse precipitates are formed cannot be obtained. Further, when it is 450 ° C or more, the recrystallization grain is coarsened, which adversely affects the moldability of the final product. The temperature of the heat treatment is preferably 200 ° C or more and 300 ° C or less, and more preferably 210 ° C or more and 280 ° C or less.
前述熱軋結束後冷軋結束前中實施的Al-Mg-Si系合 金板之熱處理的時間雖未特別限定，但為了導電率提升而以指定溫度調節時間即可，例如，以1~12小時的範圍調節時間實施熱處理即可。 Al-Mg-Si system implemented before the end of cold rolling after the completion of the hot rolling Although the time of heat treatment of the gold plate is not particularly limited, the time may be adjusted at a predetermined temperature in order to increase the conductivity. For example, the heat treatment may be performed within a range of 1 to 12 hours.
前述熱處理之後，實施冷軋進行加工硬化而強度進一步提升。 After the aforementioned heat treatment, cold rolling is performed to carry out work hardening and the strength is further improved.
前述熱處理由於提高Al-Mg-Si系合金板之冷軋所致之強度提升效果，故熱軋結束後冷軋開始前實施較佳。 Since the heat treatment described above improves the strength improvement effect by cold rolling of the Al-Mg-Si-based alloy sheet, it is preferable to perform the cold rolling after the end of hot rolling.
藉由前述熱處理後之冷軋做成指定厚度之Al-Mg-Si系合金板。熱處理後之冷軋為了強度提升以20%以上之壓延率實施較佳。熱處理後之冷軋所致之Al-Mg-Si系合金板的壓延率進一步為30%以上較佳，特別是60%以上較佳。 An Al-Mg-Si alloy plate of a predetermined thickness is formed by cold rolling after the heat treatment. The cold rolling after the heat treatment is preferably carried out at a rolling ratio of 20% or more for strength improvement. The rolling ratio of the Al-Mg-Si-based alloy sheet by cold rolling after the heat treatment is further preferably 30% or more, and particularly preferably 60% or more.
冷軋後之Al-Mg-Si系合金板亦可應需要實施洗淨。 The Al-Mg-Si alloy plate after cold rolling may also be washed as needed.
更加重視Al-Mg-Si系合金板的加工性時，亦可冷軋後實施最終退火。最終退火為了不使Al-Mg-Si系合金板之強度變得過低以200℃以下實施較佳，進一步為以180℃以下，特別是以160℃以下實施較佳。 When the workability of the Al-Mg-Si alloy plate is more important, the final annealing may be performed after cold rolling. The final annealing is preferably carried out at 200 ° C or lower so as not to increase the strength of the Al—Mg—Si-based alloy sheet, and further preferably 180° C. or lower, particularly 160° C. or lower.
前述Al-Mg-Si系合金板之最終退火的時間以可得到所需加工性及強度之方式來調節即可，例如，以1~10小時之範圍依最終退火的溫度來選擇即可。 The time for the final annealing of the Al-Mg-Si-based alloy sheet may be adjusted so as to obtain desired workability and strength. For example, it may be selected in the range of 1 to 10 hours depending on the temperature of the final annealing.
此外，本案之Al-Mg-Si系合金板的製造可以鋼捲進行，亦可以單板進行。又，在冷軋後之任意步驟可切斷合金板並以單板進行切斷後之步驟，亦可對應用途切成條。 Further, the Al-Mg-Si alloy plate of the present invention can be produced by a steel coil or a single plate. Further, in any step after cold rolling, the alloy sheet can be cut and the step of cutting the sheet can be carried out, and the strip can be cut into strips for the purpose.
以下顯示本發明之實施例及比較例。 Examples and comparative examples of the present invention are shown below.
此實施例為關於請求項1~33發明的實施例。 This embodiment is an embodiment relating to the inventions of claims 1 to 33.
藉由DC鑄造法得到表1所示之化學組成不同之鋁合金鋼胚。 Aluminum alloy steel slabs having different chemical compositions shown in Table 1 were obtained by DC casting.
對表1之化學組成編號1的鋁合金鋼胚施以面削。接著，對面削後之合金鋼胚在加熱爐中實施560℃ 5h之均質化處理後，在相同爐中變化溫度而實施540℃ 4h之熱軋前加熱。從加熱爐中取出熱軋前加熱後540℃之鋼胚，開始粗熱軋。粗熱軋中之合金板的厚度成為25mm後，自道次前的合金板溫度461℃起以平均冷卻速度80℃/分，實施粗熱軋之最終道次，做成粗熱軋完溫度243℃厚度12mm的合金板。此外，粗熱軋之最終道次中，一邊壓延一邊使合金板移動，對於壓延後之合金板的部位依序自上下實施將水噴霧至合金板的水冷所致之強制冷卻。 The aluminum alloy steel blank of chemical composition No. 1 of Table 1 was subjected to face cutting. Next, the surface-cut alloy steel blank was subjected to a homogenization treatment at 560 ° C for 5 hours in a heating furnace, and then the temperature was changed in the same furnace to carry out heating at 540 ° C for 4 h before hot rolling. The steel embryo heated at 540 ° C before hot rolling was taken out from the heating furnace, and rough hot rolling was started. After the thickness of the alloy sheet in the rough hot rolling is 25 mm, the final pass of the rough hot rolling is performed at an average cooling rate of 80 ° C / min from the alloy sheet temperature of 461 ° C before the pass, and the rough hot rolling temperature is 243. °C alloy plate with a thickness of 12 mm. Further, in the final pass of the rough hot rolling, the alloy sheet is moved while being rolled, and the portion of the rolled alloy sheet is subjected to forced cooling by spraying water to the alloy sheet in the order from the top to the bottom.
粗熱軋之後，對合金板自終熱軋前之溫度241℃起實施終熱軋，得到厚度7.0mm之合金板。終熱軋剛完成後之合金板的溫度為131℃。對終熱軋後之合金板施以215℃ 2h的熱處理後，實施壓延率98%之冷軋，得到製品板厚0.15mm的鋁合金板。 After the rough hot rolling, the alloy sheet was subjected to final hot rolling at a temperature of 241 ° C before the final hot rolling to obtain an alloy sheet having a thickness of 7.0 mm. The temperature of the alloy sheet immediately after the completion of the final hot rolling was 131 °C. After the hot-rolled alloy sheet was subjected to a heat treatment at 215 ° C for 2 hours, cold rolling was carried out at a rolling ratio of 98% to obtain an aluminum alloy sheet having a product thickness of 0.15 mm.
對表1所記載之鋁合金鋼胚施以面削後，以表2~表6所記載之條件，施以處理，得到鋁合金板。此外，與實施例1同樣地在所有實施例及比較例中均質化處理與熱軋前加熱係在相同爐中連續實施，粗熱軋最終道次後之強制冷卻，係自一邊壓延一邊使合金板移動對壓延後之合金板的部位依序自上下將水噴霧至合金板的水冷、在粗熱軋最終道次結束後進行送風冷卻的氣冷，及無強制冷卻之中選擇。又，一部分的實施例中在冷軋後實施最終退火。 The aluminum alloy steel slabs shown in Table 1 were subjected to surface-cutting, and subjected to treatment under the conditions described in Tables 2 to 6, to obtain an aluminum alloy sheet. Further, in the same manner as in Example 1, in all of the examples and the comparative examples, the homogenization treatment and the pre-hot rolling heating system were continuously carried out in the same furnace, and the forced cooling after the final hot rolling was performed, and the alloy was rolled while being rolled. The plate movement selects the portion of the rolled alloy plate from the upper and lower sides to the water cooling of the alloy plate, the air cooling after the end of the rough hot rolling, the air cooling by the air supply cooling, and the no forced cooling. Further, in some of the examples, final annealing was performed after cold rolling.
實施例14中，將粗熱軋之最終道次作為熱軋之最終道次，未實施終熱軋。 In Example 14, the final pass of the rough hot rolling was taken as the final pass of the hot rolling, and the final hot rolling was not performed.
藉由以下方法評估所得之合金板的拉伸強度、導電率、加工性。 The tensile strength, electrical conductivity, and workability of the obtained alloy sheets were evaluated by the following methods.
拉伸強度係對於JIS5號試驗片於常溫藉由常法來測定。 The tensile strength was measured by a usual method at room temperature for JIS No. 5 test piece.
導電率係以將國際上採取之退火標準軟銅(體積低效率1.7241×10-2μΩm)的導電率作為100%IACS時的相對值(%IACS)來求出。 The electrical conductivity was determined by taking the electrical conductivity of the annealed standard soft copper (volume low efficiency 1.7241 × 10 -2 μΩm) taken internationally as a relative value (% IACS) at 100% IACS.
加工性係將彎曲角度定為90°，合金板厚度為0.4mm以上時將各自的合金板板厚定為彎曲內側半徑，合金板厚度未達0.4mm時彎曲內側半徑定為0，實施藉由JIS Z 2248金屬材料彎曲試驗方法之6.3V形塊法的彎曲試驗，未發生破裂者評估為○、發生破裂者評估為×。 The processing property is set to a bending angle of 90°, and when the thickness of the alloy plate is 0.4 mm or more, the thickness of each alloy plate is set as the inner radius of the bending, and when the thickness of the alloy plate is less than 0.4 mm, the inner radius of the bending is set to 0. The bending test of the 6.3 V-block method of the JIS Z 2248 metal material bending test method is evaluated as ○ without cracking and × when cracking occurs.
拉伸強度、導電率及加工性的評估結果表示於表2~表6。 The evaluation results of tensile strength, electrical conductivity, and workability are shown in Tables 2 to 6.
相對於具有本案規定之化學組成，且熱軋剛結束後之合金板的表面溫度為230℃以下且熱軋結束後冷軋結束前之熱處理溫度為200℃以上400℃以下之範圍內的實施例中，拉伸強度及導電率顯示高值且加工性亦良好，本案規定之化學組成、熱軋剛結束後之合金板的表面溫度或熱軋結束後冷軋結束前的熱處理溫度之至少一者未滿足本案規定範圍之比較例，其拉伸強度或導電率之至少一者比實施例差，亦有加工性差者。 Example with respect to the chemical composition having the chemical composition specified in the present invention, and the surface temperature of the alloy sheet immediately after the hot rolling is 230 ° C or lower and the heat treatment temperature before the end of the cold rolling is 200 ° C or higher and 400 ° C or lower Among them, the tensile strength and the electrical conductivity show high values and the workability is also good, and the chemical composition specified in the present case, the surface temperature of the alloy sheet immediately after the hot rolling, or the heat treatment temperature before the end of the cold rolling after the hot rolling is at least one of In the comparative example which did not satisfy the scope of the present case, at least one of the tensile strength and the electrical conductivity was inferior to the examples, and the workability was poor.
此實施例為關於請求項34~76發明的實施例。 This embodiment is an embodiment relating to the invention of claims 34-76.
藉由DC鑄造法得到表7所示之化學組成不同之鋁合金鋼胚。此外，包含稀土類之化學組成編號120的鑄錠於鑄造中使用包含美鈰合金的原料。 Aluminum alloy steel slabs having different chemical compositions shown in Table 7 were obtained by DC casting. Further, an ingot containing a chemical composition number 120 of a rare earth is used as a raw material containing a bismuth alloy in casting.
對表7之化學組成編號101之鋁合金鋼胚施以面削。接著，對面削後的合金鋼胚在加熱爐中實施570℃ 5h的均質化處理後，在相同爐中變化溫度而實施540℃ 4h之熱軋前加熱。從加熱爐中取出熱軋前加熱後540℃之鋼胚，開始粗熱軋。粗熱軋中之合金板的厚度成為25mm後，自道次前的合金板溫度460℃起以平均冷卻速度80℃/分，實施粗熱軋之最終道次，做成粗熱軋完溫度242℃厚度12mm的合金板。此外，粗熱軋之最終道次中，一邊壓延一邊使合金板移動，對於壓延後之合金板的部位依序自上下實施將水噴霧至合金板的水冷所致之強制冷卻。 The aluminum alloy steel blank of chemical composition No. 101 of Table 7 was subjected to face cutting. Next, the surface-cut alloy steel blank was subjected to a homogenization treatment at 570 ° C for 5 hours in a heating furnace, and then the temperature was changed in the same furnace to carry out heating before hot rolling at 540 ° C for 4 hours. The steel embryo heated at 540 ° C before hot rolling was taken out from the heating furnace, and rough hot rolling was started. After the thickness of the alloy sheet in the rough hot rolling is 25 mm, the final pass of the rough hot rolling is performed at an average cooling rate of 80 ° C / min from the temperature of the alloy sheet before the pass, and the rough hot rolling temperature is 242. °C alloy plate with a thickness of 12 mm. Further, in the final pass of the rough hot rolling, the alloy sheet is moved while being rolled, and the portion of the rolled alloy sheet is subjected to forced cooling by spraying water to the alloy sheet in the order from the top to the bottom.
粗熱軋之後，對合金板自終熱軋前之溫度240℃起實施終熱軋，得到厚度7.0mm之合金板。終熱軋剛完成後之合金板的溫度為130℃。對終熱軋後之合金板施以215℃ 2h的熱處理後，實施壓延率98%之冷軋，得到製品板厚0.15mm的鋁合金板。 After the rough hot rolling, the alloy sheet was subjected to final hot rolling at a temperature of 240 ° C before the final hot rolling to obtain an alloy sheet having a thickness of 7.0 mm. The temperature of the alloy sheet immediately after the completion of the final hot rolling was 130 °C. After the hot-rolled alloy sheet was subjected to a heat treatment at 215 ° C for 2 hours, cold rolling was carried out at a rolling ratio of 98% to obtain an aluminum alloy sheet having a product thickness of 0.15 mm.
對表7所記載之鋁合金鋼胚施以面削後，以表8~表12所記載之條件，施以處理，得到鋁合金板。此外，與實施例101同樣地在所有實施例及比較例中均質化處理與熱軋前加熱係在相同爐中連續實施，粗熱軋最終道次後之強制冷卻，係自一邊壓延一邊使合金板移動對壓延後之合金板的部位依序自上下將水噴霧至合金板的水冷、在粗熱軋最終道次結束後進行送風冷卻的氣冷，及無強制冷卻之中選擇。又，一部分的實施例中在冷軋後實施最終退火。 The aluminum alloy steel slabs shown in Table 7 were subjected to surface-cutting, and subjected to treatment under the conditions described in Tables 8 to 12 to obtain an aluminum alloy sheet. Further, in the same manner as in Example 101, in all of the examples and the comparative examples, the homogenization treatment and the pre-hot rolling heating system were continuously carried out in the same furnace, and the forced cooling after the final pass of the rough hot rolling was performed by rolling the alloy while rolling. The plate movement selects the portion of the rolled alloy plate from the upper and lower sides to the water cooling of the alloy plate, the air cooling after the end of the rough hot rolling, the air cooling by the air supply cooling, and the no forced cooling. Further, in some of the examples, final annealing was performed after cold rolling.
實施例114中，將粗熱軋之最終道次作為熱軋之最終道次，未實施終熱軋。 In Example 114, the final pass of the rough hot rolling was taken as the final pass of the hot rolling, and the final hot rolling was not performed.
藉由以下方法評估所得之合金板的拉伸強度、導電率、加工性。 The tensile strength, electrical conductivity, and workability of the obtained alloy sheets were evaluated by the following methods.
拉伸強度係對於JIS5號試驗片於常溫藉由常法來測定。 The tensile strength was measured by a usual method at room temperature for JIS No. 5 test piece.
導電率係以將國際上採取之退火標準軟銅(體積低效率1.7241×10-2μΩm)的導電率作為100%IACS時的相對值(%IACS)來求出。 The electrical conductivity was determined by taking the electrical conductivity of the annealed standard soft copper (volume low efficiency 1.7241 × 10 -2 μΩm) taken internationally as a relative value (% IACS) at 100% IACS.
加工性係將彎曲角度定為90°，合金板厚度為0.4mm以上時將各自的合金板板厚定為彎曲內側半徑，合金板厚度未達0.4mm時彎曲內側半徑定為0，實施藉由JIS Z 2248金屬材料彎曲試驗方法之6.3V形塊法的彎曲試驗，未發生破裂者評估為○、發生破裂者評估為×。 The processing property is set to a bending angle of 90°, and when the thickness of the alloy plate is 0.4 mm or more, the thickness of each alloy plate is set as the inner radius of the bending, and when the thickness of the alloy plate is less than 0.4 mm, the inner radius of the bending is set to 0. The bending test of the 6.3 V-block method of the JIS Z 2248 metal material bending test method is evaluated as ○ without cracking and × when cracking occurs.
拉伸強度、導電率及加工性的評估結果表示於表8~表12。 The evaluation results of tensile strength, electrical conductivity, and workability are shown in Tables 8 to 12.
相對於具有本案規定之化學組成，且熱軋剛結束後之合金板的表面溫度為230℃以下且熱軋結束後冷軋結束前之熱處理溫度為200℃以上400℃以下之範圍內的實施例中，拉伸強度及導電率顯示高值且加工性亦良好，本案規定之化學組成、熱軋剛結束後之合金板的表面溫度或熱軋結束後冷軋結束前的熱處理溫度之至少一者未滿足本案規定範圍之比較例，其拉伸強度或導電率之至少一者比實施例差，亦有加工性差者。 Example with respect to the chemical composition having the chemical composition specified in the present invention, and the surface temperature of the alloy sheet immediately after the hot rolling is 230 ° C or lower and the heat treatment temperature before the end of the cold rolling is 200 ° C or higher and 400 ° C or lower Among them, the tensile strength and the electrical conductivity show high values and the workability is also good, and the chemical composition specified in the present case, the surface temperature of the alloy sheet immediately after the hot rolling, or the heat treatment temperature before the end of the cold rolling after the hot rolling is at least one of In the comparative example which did not satisfy the scope of the present case, at least one of the tensile strength and the electrical conductivity was inferior to the examples, and the workability was poor.
本案係伴隨皆於2016年3月30日申請之日本專利申請案之特願2016-67357號及特願2016-67358號的優先權 主張者，其揭示內容直接構成本案之一部分。 The priority of the Japanese Patent Application No. 2016-67357 and Special Purpose 2016-67358, which were filed on March 30, 2016 The claimer’s disclosure directly forms part of the case.
應有所認知的是，在此使用的用語及表現是為了說明而使用的，而不是為了限定性地解釋而使用的，亦不排除在此公開並敘述之特徵事項的任何均等物，且亦容許在本發明所請求的範圍內的各種變形。 It is to be understood that the terms and expressions used herein are for the purpose of description and are not intended to Various modifications are possible within the scope of the invention as claimed.
本發明能夠以多種不同方式具體化，但本公開應認為是提供本發明原理的實施例，且在瞭解到該等實施例並不旨在將本發明限定於此處記載且/或圖示之較佳實施型態的基礎上，將多個圖示實施型態記載於此。 The present invention can be embodied in a variety of different ways, but the present disclosure is intended to be illustrative of the embodiments of the present invention. In addition to the preferred embodiments, a plurality of illustrated embodiments are described herein.
儘管在此記載著幾個本發明的實施型態，但是本發明並不限定於此處記載的各種較佳實施型態，並且可由該業者基於本公開內容而辨認，且亦包含具有均等的要素、修正、刪除、組合(例如，跨各種實施型態之特徵的組合)、改良及/或變更的全部實施型態。請求項的限定事項應基於該請求項使用的用語作廣泛解釋，不應限定為本說明書或本申請的審查階段中記載的實施例，此類實施例應解讀為非排他性。 Although a few embodiments of the present invention are described herein, the present invention is not limited to the various preferred embodiments described herein, and can be recognized by the applicant based on the present disclosure, and also includes equal elements. Modifications, deletions, combinations (eg, combinations of features across various implementations), improvements, and/or changes to all implementations. The limitation of the claim item should be interpreted broadly based on the terms used in the claim, and should not be construed as limiting the embodiments described in this specification or the review stage of the present application. Such embodiments should be construed as non-exclusive.
本發明可利用於Al-Mg-Si系合金板的製造。 The present invention can be utilized in the production of an Al-Mg-Si alloy plate.
Claims (72)
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2016067358A JP6774200B2 (en) | 2016-03-30 | 2016-03-30 | Manufacturing method of Al-Mg-Si based alloy plate |
| JP2016067357A JP2017179454A (en) | 2016-03-30 | 2016-03-30 | MANUFACTURING METHOD OF Al-Mg-Si-BASED ALLOY SHEET |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| TW201738390A true TW201738390A (en) | 2017-11-01 |
Family
ID=59962959
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| TW106103837A TW201738390A (en) | 2016-03-30 | 2017-02-06 | Method for producing al-mg-Si alloy plate |
Country Status (3)
| Country | Link |
|---|---|
| CN (1) | CN108884542B (en) |
| TW (1) | TW201738390A (en) |
| WO (1) | WO2017168892A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| TWI762737B (en) * | 2017-12-12 | 2022-05-01 | 日商日本輕金屬股份有限公司 | Pellicle frame for fpd (flat panel display) and manufacturing method thereof |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111705244A (en) * | 2020-07-13 | 2020-09-25 | 江苏亚太航空科技有限公司 | Manufacturing method of high-conductivity aluminum alloy round bar |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2003074750A1 (en) * | 2002-03-01 | 2003-09-12 | Showa Denko K.K. | PROCESS FOR PRODUCING Al-Mg-Si ALLOY PLATE, Al-Mg-Si ALLOY PLATE AND Al-Mg-Si ALLOY MATERIAL |
| ATE507316T1 (en) * | 2002-03-01 | 2011-05-15 | Showa Denko Kk | METHOD FOR PRODUCING AN AL-MG-SI ALLOY PLATE |
| JP5113318B2 (en) * | 2004-04-13 | 2013-01-09 | 古河スカイ株式会社 | Aluminum alloy plate for forming and method for producing the same |
| JP2016160516A (en) * | 2015-03-04 | 2016-09-05 | 株式会社神戸製鋼所 | Aluminum alloy sheet |
-
2016
- 2016-12-26 WO PCT/JP2016/088717 patent/WO2017168892A1/en active Application Filing
- 2016-12-26 CN CN201680083568.1A patent/CN108884542B/en active Active
-
2017
- 2017-02-06 TW TW106103837A patent/TW201738390A/en unknown
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| TWI762737B (en) * | 2017-12-12 | 2022-05-01 | 日商日本輕金屬股份有限公司 | Pellicle frame for fpd (flat panel display) and manufacturing method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN108884542A (en) | 2018-11-23 |
| CN108884542B (en) | 2022-03-01 |
| WO2017168892A1 (en) | 2017-10-05 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN108699641B (en) | Al-Mg-Si alloy material, Al-Mg-Si alloy sheet, and method for producing Al-Mg-Si alloy sheet | |
| JPWO2005056859A1 (en) | Method for producing Al-Mg-Si alloy plate excellent in bake hardness and hemmability | |
| JP2017179457A (en) | Al-Mg-Si-BASED ALLOY MATERIAL | |
| JP6695725B2 (en) | Al-Mg-Si alloy plate | |
| JP6774196B2 (en) | Al-Mg-Si based alloy material | |
| CN110872664A (en) | Al-Mg-Si alloy plate | |
| JP2017179454A (en) | MANUFACTURING METHOD OF Al-Mg-Si-BASED ALLOY SHEET | |
| JP6774199B2 (en) | Manufacturing method of Al-Mg-Si based alloy plate | |
| JP2020033604A (en) | MANUFACTURING METHOD OF Al-Mg-Si-BASED ALLOY SHEET | |
| JP7442304B2 (en) | Aluminum alloy rolled material with excellent thermal conductivity, electrical conductivity, and strength, and its manufacturing method | |
| CN110872665B (en) | Al-Mg-Si alloy plate | |
| JP6718276B2 (en) | Method for manufacturing Al-Mg-Si alloy plate | |
| TW201738390A (en) | Method for producing al-mg-Si alloy plate | |
| JP2017179452A (en) | MANUFACTURING METHOD OF Al-Mg-Si-BASED ALLOY SHEET | |
| JP2017179456A (en) | Al-Mg-Si-BASED ALLOY MATERIAL | |
| TW201742931A (en) | Method for producing Al-Mg-Si alloy plate | |
| JP6774197B2 (en) | Al-Mg-Si based alloy material | |
| JP2017179444A (en) | Al-Mg-Si-BASED ALLOY SHEET | |
| JP6774200B2 (en) | Manufacturing method of Al-Mg-Si based alloy plate | |
| JP6774198B2 (en) | Al-Mg-Si based alloy plate | |
| JP2020033609A (en) | Al-Mg-Si-BASED ALLOY SHEET | |
| JP2020033606A (en) | MANUFACTURING METHOD OF Al-Mg-Si-BASED ALLOY SHEET | |
| JP6718275B2 (en) | Method for manufacturing Al-Mg-Si alloy plate | |
| JP2017179451A (en) | MANUFACTURING METHOD OF Al-Mg-Si-BASED ALLOY SHEET | |
| JP2017179450A (en) | MANUFACTURING METHOD OF Al-Mg-Si-BASED ALLOY SHEET |