JP2747770B2 - Aluminum alloy sheet for blinds and method of manufacturing the same - Google Patents
Aluminum alloy sheet for blinds and method of manufacturing the sameInfo
- Publication number
- JP2747770B2 JP2747770B2 JP5077703A JP7770393A JP2747770B2 JP 2747770 B2 JP2747770 B2 JP 2747770B2 JP 5077703 A JP5077703 A JP 5077703A JP 7770393 A JP7770393 A JP 7770393A JP 2747770 B2 JP2747770 B2 JP 2747770B2
- Authority
- JP
- Japan
- Prior art keywords
- aluminum alloy
- strength
- cold rolling
- blinds
- less
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims description 33
- 238000004519 manufacturing process Methods 0.000 title claims description 8
- 238000005097 cold rolling Methods 0.000 claims description 34
- 239000011248 coating agent Substances 0.000 claims description 13
- 238000000576 coating method Methods 0.000 claims description 13
- 229910052802 copper Inorganic materials 0.000 claims description 12
- 238000000137 annealing Methods 0.000 claims description 10
- 229910052749 magnesium Inorganic materials 0.000 claims description 8
- 229910052748 manganese Inorganic materials 0.000 claims description 8
- 239000012535 impurity Substances 0.000 claims description 7
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 239000000956 alloy Substances 0.000 description 23
- 238000010438 heat treatment Methods 0.000 description 23
- 239000000463 material Substances 0.000 description 22
- 239000000243 solution Substances 0.000 description 21
- 229910045601 alloy Inorganic materials 0.000 description 18
- 230000007423 decrease Effects 0.000 description 18
- 239000003973 paint Substances 0.000 description 17
- 238000012360 testing method Methods 0.000 description 16
- 150000001875 compounds Chemical class 0.000 description 12
- 238000005096 rolling process Methods 0.000 description 12
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 9
- 238000005098 hot rolling Methods 0.000 description 8
- 230000000694 effects Effects 0.000 description 7
- 238000000034 method Methods 0.000 description 7
- 229910019086 Mg-Cu Inorganic materials 0.000 description 5
- 238000005482 strain hardening Methods 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 238000001816 cooling Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 230000007547 defect Effects 0.000 description 3
- 238000011156 evaluation Methods 0.000 description 3
- WABPQHHGFIMREM-UHFFFAOYSA-N lead(0) Chemical compound [Pb] WABPQHHGFIMREM-UHFFFAOYSA-N 0.000 description 3
- 230000001376 precipitating effect Effects 0.000 description 3
- 229910052782 aluminium Inorganic materials 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 230000005496 eutectics Effects 0.000 description 2
- 238000000265 homogenisation Methods 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 102220253765 rs141230910 Human genes 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 229910018131 Al-Mn Inorganic materials 0.000 description 1
- 229910018461 Al—Mn Inorganic materials 0.000 description 1
- 229910017818 Cu—Mg Inorganic materials 0.000 description 1
- 229910002551 Fe-Mn Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000005259 measurement Methods 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
- 238000010422 painting Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Landscapes
- Blinds (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は、ブラインド用アルミニ
ウム合金板材およびその製造方法、とくに塗装焼付処理
を施した後においても強度低下が少ないブラインド用ア
ルミニウム合金板材およびその製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an aluminum alloy sheet for blinds and a method for producing the same, and more particularly to an aluminum alloy sheet for blinds which exhibits a small reduction in strength even after a paint baking treatment.
【０００２】[0002]
【従来の技術】ブラインド用材料にはある程度以上の強
度および耐食性が要求されることから、アルミニウム合
金の薄板が多く使用されており、従来ＡＡ5052(Al-2.5
％Mg-0.25 ％Cr系) 、5086(Al-4 ％Mg-0.5％Mn-0.15 ％
Cr系) 、5182(Al-4.5 ％Mg-0.35 ％Mn系) などのＡｌ−
Ｍｇ系アルミニウム合金の0.1 〜0.2mm 厚の圧延板が用
いられてきた。一般に、ブラインドは塗装仕上げされて
使用されるものであるから、ブラインド用アルミニウム
合金材料としては、塗装後の焼付処理で軟化しない材料
が望まれているが、上記のアルミニウム合金は、通常行
われる200 〜230℃の温度に40〜50秒保持される塗装焼
付処理において強度とくに耐力の低下が生じ易く、ブラ
インドとしての性能を低下させることが少なくない。2. Description of the Related Art Since blind materials require a certain level of strength and corrosion resistance, thin sheets of aluminum alloy are often used.
% Mg-0.25% Cr-based), 5086 (Al-4% Mg-0.5% Mn-0.15%
Cr-based), 5182 (Al-4.5% Mg-0.35% Mn-based)
Rolled sheets of Mg-based aluminum alloy having a thickness of 0.1 to 0.2 mm have been used. In general, since the blind is used after being painted, the aluminum alloy material for the blind is desired to be a material that does not soften by baking treatment after painting. In paint baking treatment, which is performed at a temperature of about 230 ° C. for 40 to 50 seconds, the strength, especially the proof stress, tends to be reduced, and the performance as a blind is often reduced.
【０００３】強度特性を改善したブラインド用アルミニ
ウム合金材料として、4 ％Ｍｇ、1％Ｚｎを含むＡｌ合
金（特開昭60-251245 号) 、これにさらに1 ％Ｃｕを添
加したＡｌ合金（特開昭61-15937号) 、2 ％Ｃｕ、1 ％
Ｍｇ、1 ％Ｓｉを含むＡｌ合金（特開昭61-15938号) 、
Ａｌ−Ｍｇ−Ｍｎ−Ｆｅをベ−スとする合金（特開平1-
205050、205051、205052号) 、2 ％Ｍｇ、1 ％Ｍｎ、0.
35％Ｃｕを含むＡｌ合金（特開平4-88145 号) が開発さ
れており、製造方法としては、2 ％Ｍｇ、1 ％Ｍｎ、0.
35％Ｃｕを含むＡｌ合金を熱間圧延後、冷間圧延の途中
で溶体化処理し、最終圧延加工度を高くして強度を上げ
る方法（特開平4-88145 号) 、中間熱処理の前後に1
次、2 次の冷間圧延を行い、加工度を大きくすることに
より強度を付与する方法( 特開平2-25546 号) が提案さ
れている。As an aluminum alloy material for blinds having improved strength characteristics, an Al alloy containing 4% Mg and 1% Zn (Japanese Patent Application Laid-Open No. 60-251245), and an Al alloy further containing 1% Cu (Japanese Patent Application Laid-open No. No. 61-15937), 2% Cu, 1%
Al alloy containing Mg and 1% Si (JP-A-61-15938),
Alloys based on Al-Mg-Mn-Fe
205050, 205051, 205052), 2% Mg, 1% Mn, 0.
An Al alloy containing 35% Cu (Japanese Patent Application Laid-Open No. 4-88145) has been developed. The manufacturing method is as follows: 2% Mg, 1% Mn, 0.1% Mn.
A method in which an Al alloy containing 35% Cu is hot-rolled and then subjected to a solution treatment in the middle of cold rolling to increase the final rolling workability and increase the strength (Japanese Patent Laid-Open No. 4-88145). 1
Next, there has been proposed a method (Japanese Patent Application Laid-Open No. 2-25546) of imparting strength by performing secondary and secondary cold rolling to increase the degree of work.
【０００４】しかしながら、これらのアルミニウム合金
では、強度を確保するために冷間加工率を高めたとき、
例えば70％以上の圧延加工を行った場合には、最終板厚
が薄いため板端部の割れが生じ易くなって材料の歩留り
が低下し、圧延不能になることもある。例えば90％以上
の加工度が必要なものでは、圧延パス回数が増加して作
業能率を低下させるという問題もある。However, in these aluminum alloys, when the cold working rate is increased to secure the strength,
For example, when the rolling process is performed at 70% or more, since the final plate thickness is thin, cracks at the plate edge are apt to occur, and the yield of the material is reduced, and the rolling cannot be performed in some cases. For example, in the case where a working ratio of 90% or more is required, there is a problem that the number of rolling passes is increased and the working efficiency is reduced.
【０００５】また、最近は、居住性の向上のために、カ
ラフルなブラインドが求められており、１コート目と２
コート目の色を変えて塗装焼付処理を２回行う（２コー
ト２ベーク）から、強度低下はさらに大きくなり易く、
ますます加熱処理後の強度低下が小さいブラインド用ア
ルミニウム合金材料の開発が要請されている。[0005] Recently, colorful blinds have been required in order to improve the comfort of living.
Since the paint baking treatment is performed twice by changing the color of the coat (2 coats and 2 bake), the strength decrease is more likely to increase,
There is a growing demand for aluminum alloy materials for blinds that have a small decrease in strength after heat treatment.
【０００６】[0006]
【発明が解決しようとする課題】本発明は、ブラインド
用アルミニウム合金材における従来の問題点を解消する
とともに上記の開発要請に応えるために、塗装焼付処理
後の強度と成分元素の組み合わせおよびこれら元素の塗
装焼付処理温度における析出態様、冷間加工性と添加元
素の組み合わせについて研究を行った結果、Ｓｉ、Ｍｇ
およびＣｕ量を調整し、塗装焼付処理時、析出するＭｇ
をすべてＭｇ2 Ｓｉ相またはＡｌ−Ｍｇ−Ｃｕ系化合物
として析出させるとともに、余剰のＳｉ、Ｃｕの含有に
より合金の強度を高め、さらにＭｇの含有量を必要最小
限に抑え、これらの成分の組み合わせの中でＴｉを添加
することにより冷間加工性を高めることが可能であるこ
とを見出したことに基づいてなされたものであり、最終
冷間圧延加工率を高めても板端部に割れを生じることが
なく、圧延１パスでの圧下量を大きくできて圧延パス回
数の増加も避けられ、塗装焼付処理後の強度低下も少な
いブラインド用アルミニウム合金板材を提供することを
目的とする。SUMMARY OF THE INVENTION The present invention solves the conventional problems in aluminum alloy materials for blinds and, in order to meet the above-mentioned demands for development, a combination of strength and component elements after a paint baking treatment and a combination of these elements. As a result of research on the combination of precipitation mode, cold workability and additional elements at the paint baking treatment temperature, Si, Mg
And the amount of Cu deposited during the coating baking process
Is precipitated as Mg 2 Si phase or Al-Mg-Cu-based compound, the strength of the alloy is increased by the addition of excess Si and Cu, and the content of Mg is suppressed to the minimum necessary. It has been made based on the finding that the cold workability can be enhanced by adding Ti in the steel sheet. An object of the present invention is to provide an aluminum alloy sheet material for blinds that does not occur, can reduce the amount of rolling in one rolling pass, can avoid an increase in the number of rolling passes, and has a small decrease in strength after baking.
【０００７】[0007]
【課題を解決するための手段】上記の目的を達成するた
めの本発明によるブラインド用アルミニウム合金板材お
よびその製造方法は、Ｓｉ1.0 〜1.5 ％（重量％、以下
同じ）、Ｍｇ0.5 〜0.8 ％、Ｍｎ0.8 〜1.2 ％、Ｔｉ0.
05〜0.20％およびＣｕ0.1 〜0.3 ％を含有し、不純物と
してのＦｅを0.30％以下に制限し、残部Ａｌおよび不可
避不純物からなるアルミニウム合金であって、耐力が40
0 ＭＰａ以下、電気抵抗率が1.3 μΩ・cm以上であり、
230 ℃以下で50秒以上の塗装焼付処理を行った後におけ
る耐力が350 ＭＰａ以上であること、およびＳｉ1.0 〜
1.5 ％、Ｍｇ0.5 〜0.8 ％、Ｍｎ0.8 〜1.2 ％、Ｔｉ0.
05〜0.20％、Ｃｕ0.1 〜0.3 ％を含有し、不純物として
のＦｅを0.30％以下に制限し、残部Ａｌおよび不可避不
純物からなるアルミニウム合金を、熱間圧延ならびに冷
間圧延し、連続焼鈍炉により500 〜550 ℃に加熱する溶
体化処理を行った後、加工率70〜85％の最終冷間圧延を
行い、230 ℃以下で50秒以上の塗装焼付処理を行った後
における耐力を350 ＭＰａ以上とすることを構成上の特
徴とする。The aluminum alloy sheet for blinds and the method for producing the same according to the present invention for achieving the above object are provided with Si of 1.0 to 1.5% (% by weight, the same applies hereinafter) and Mg of 0.5 to 0.8. %, Mn 0.8-1.2%, Ti0.
An aluminum alloy containing 0.05 to 0.20% and Cu 0.1 to 0.3%, Fe as an impurity is limited to 0.30% or less, and the balance is Al and unavoidable impurities.
0 MPa or less, electric resistivity is 1.3 μΩcm or more,
The proof stress after performing the coating baking treatment at 230 ° C or less for 50 seconds or more is 350 MPa or more, and the Si1.0
1.5%, Mg 0.5-0.8%, Mn 0.8-1.2%, Ti0.
An aluminum alloy containing 0.05 to 0.20%, Cu 0.1 to 0.3%, Fe as an impurity is limited to 0.30% or less, and an aluminum alloy consisting of the balance of Al and inevitable impurities is hot-rolled and cold-rolled to form a continuous annealing furnace. And then cold-rolled at a working rate of 70-85%, and the proof stress after performing a coating baking treatment at 230 ° C or lower for 50 seconds or more is 350 MPa. The above is a feature of the configuration.
【０００８】本発明におけるアルミニウム合金の成分限
定理由について説明すると、Ｓｉは、塗装焼付処理温度
（200 〜230 ℃) において、ＭｇとともにＭｇ2 Ｓｉ相
を析出させ、塗装焼付処理を行った後の合金の強度低下
を軽減するのに効果がある。好ましい含有範囲は1.0 〜
1.5 ％であり、1.0 ％未満では、本発明のＭｇ含有量が
0.5 〜0.8 ％と少ないため、Ｍｇ2 Ｓｉ相の形成が少な
くなり塗装焼付処理後の強度が低下する。1.5 ％を越え
ると、合金の延性が低下し、冷間圧延加工において板端
部に割れが生じ易くなる。The reasons for limiting the components of the aluminum alloy according to the present invention will be described. Si is obtained by precipitating an Mg 2 Si phase together with Mg at a coating baking temperature (200 to 230 ° C.) and subjecting the alloy to a coating baking treatment. This is effective in reducing the decrease in strength. The preferred content range is 1.0 to
1.5%, and if less than 1.0%, the Mg content of the present invention is
Since it is as small as 0.5 to 0.8%, the formation of Mg 2 Si phase is reduced, and the strength after baking treatment is reduced. If it exceeds 1.5%, the ductility of the alloy decreases, and cracks tend to occur at the end of the sheet in cold rolling.
【０００９】Ｍｇは、ＳｉやＣｕとともに塗装焼付処理
温度でＭｇ2 Ｓｉ相，Ａｌ−Ｍｇ−Ｃｕ系化合物を析出
させ、塗装焼付処理を行った後の合金の強度低下を軽減
するのに効果がある。好ましい含有範囲は0.5 〜0.8 ％
であり、0.5 ％未満では、Ｍｇ2 Ｓｉ相やＡｌ−Ｍｇ−
Ｃｕ系化合物の形成が少なく塗装焼付処理後に強度低下
が生じる。0.8 ％を越えると、冷間圧延における加工硬
化が大きくなって１パスでの圧下量が少なくなり、圧延
パス数の増加や圧延板端部の割れ発生の原因となる。Mg, together with Si and Cu, precipitates an Mg 2 Si phase and an Al—Mg—Cu compound at a paint baking treatment temperature, and is effective in reducing a decrease in the strength of the alloy after the paint baking treatment. is there. The preferred content range is 0.5 to 0.8%.
If less than 0.5%, Mg 2 Si phase or Al-Mg-
The formation of the Cu-based compound is small and the strength is reduced after the baking treatment. If it exceeds 0.8%, the work hardening in cold rolling increases, and the amount of reduction in one pass decreases, leading to an increase in the number of rolling passes and the occurrence of cracks at the ends of the rolled sheet.
【００１０】Ｍｎは、溶体化処理および塗装焼付処理に
おいてＡｌ−Ｍｎ系化合物を析出させ、合金材料に耐熱
性を与え、塗装焼付処理後の強度低下を軽減する効果が
あり、0.8 〜1.2 ％の範囲で含有される。0.8 ％未満で
は、Ｍｇ量が少ないこともあってその効果が小さく、1.
2 ％を越えて含有すると、冷間圧延における加工硬化が
大きくなって１パスでの圧下量が大きくできないため、
圧延パス数が増加し、圧延板端部に割れが生じ易くな
る。さらに、Ａｌ−Ｆｅ−Ｍｎ系の粗大晶出物を形成
し、熱間圧延や冷間圧延時に割れを生じ易くするととも
に、ピンホールなどの欠陥発生の原因ともなる。Mn has the effect of precipitating Al-Mn compounds in solution treatment and paint baking to impart heat resistance to the alloy material and to reduce the reduction in strength after paint baking, and has an effect of 0.8 to 1.2%. It is contained in the range. If it is less than 0.8%, the effect is small due to the small amount of Mg.
If the content exceeds 2%, the work hardening in cold rolling increases, and the amount of reduction in one pass cannot be increased.
The number of rolling passes increases, and cracks tend to occur at the ends of the rolled plate. In addition, Al-Fe-Mn-based coarse crystals are formed, which tend to cause cracks during hot rolling and cold rolling, and cause defects such as pinholes.
【００１１】Ｆｅは、Ａｌ−Ｍｎ−Ｆｅ系の粗大晶出物
を形成して、熱間圧延や冷間圧延時に割れを生じ易く
し、最終圧延板材にピンホールなどの欠陥を発生させる
原因となるので、Ｍｎによる塗装焼付処理後の強度低下
軽減の効果を得るために、Ｆｅ含有量はできるだけ低く
抑えるのが望ましいが、Ｆｅ分を低くするには高純アル
ミニウム地金の使用が必要となって製造コストが大とな
ることを考慮し、本発明の合金組成においては、0.3 ％
を上限とする。[0011] Fe forms coarse Al-Mn-Fe crystallized substances, which tend to cause cracks during hot rolling or cold rolling, and cause defects such as pinholes in the final rolled sheet. Therefore, it is desirable to keep the Fe content as low as possible in order to obtain the effect of reducing the strength reduction after the coating baking treatment with Mn, but it is necessary to use a high-purity aluminum ingot to reduce the Fe content. Considering that the production cost is high, the alloy composition of the present invention is 0.3%
Is the upper limit.
【００１２】Ｔｉは、合金の鋳塊組織を微細化し、熱間
圧延および溶体化処理時に微細結晶粒組織を形成して、
冷間圧延において板端部に割れを発生させることなく、
最終冷間圧延率を大きくすることを可能とする。好まし
い添加範囲は0.05〜0.20％であり、0.05％未満ではその
効果が小さく、0.20％を越えるとＡｌ3 Ｔｉの粗大化合
物が形成し、熱間圧延や冷間圧延時に割れが生じ易くな
り、最終圧延板材にピンホールなどの欠陥を発生させる
原因ともなる。Ti refines the ingot structure of the alloy and forms a fine grain structure during hot rolling and solution treatment.
Without generating cracks at the plate edge in cold rolling,
It is possible to increase the final cold rolling rate. A preferable addition range is 0.05 to 0.20%, and if the addition is less than 0.05%, the effect is small, and if it exceeds 0.20%, a coarse compound of Al 3 Ti is formed, and cracks are easily generated at the time of hot rolling or cold rolling. It also causes defects such as pinholes in the rolled sheet material.
【００１３】Ｃｕは、塗装焼付処理温度においてＭｇと
ともにＡｌ−Ｍｇ−Ｃｕ系化合物を析出させ、合金の強
度低下を軽減させる効果がある。好ましい含有範囲は0.
1 〜0.3 ％であり、0.1 ％未満ではＡｌ−Ｍｇ−Ｃｕ系
化合物の析出量が少なく、強度低下軽減の効果が小さ
い。0.3 ％を越えると、合金の延性が低下し、冷間圧延
加工において板端部に割れが生じ易くなる。[0013] Cu has the effect of precipitating an Al-Mg-Cu-based compound together with Mg at the coating baking treatment temperature, thereby reducing the decrease in the strength of the alloy. The preferred content range is 0.
When the content is less than 0.1%, the precipitation amount of the Al-Mg-Cu-based compound is small, and the effect of reducing the decrease in strength is small. If it exceeds 0.3%, the ductility of the alloy decreases, and cracks tend to occur at the end of the sheet in cold rolling.
【００１４】本発明のアルミニウム合金板材は上記の組
成を有し、性状的要件として、耐力が４００ＭＰａ以
下、電気抵抗率が１．３μΩ・ｃｍ以上であることが必
須である。耐力は最終冷間圧延の加工率を高めることに
より上昇するが、耐力が４００ＭＰａを越えるようにな
ると、加工中に板端部に割れが生じ易くなり、歩留りが
低下するとともに圧延不能となることもあり好ましくな
い。電気抵抗率は、塗装焼付処理時における合金の耐軟
化特性に影響するもので、Ｓｉ、Ｍｇ、Ｃｕ等の固溶量
が多くなると大きくなり、固溶量を示す指標となるもの
であり、１．３μΩ・ｃｍ以上に限定するのが好まし
い。The aluminum alloy sheet of the present invention has the above-mentioned composition, and it is essential that the proof strength is 400 MPa or less and the electric resistivity is 1.3 μΩ · cm or more. The yield strength is increased by increasing the working ratio of the final cold rolling, but when the yield strength exceeds 400 MPa, cracks are likely to occur at the end of the plate during processing, the yield decreases, and rolling may not be possible. There is not preferred. The electrical resistivity affects the softening resistance of the alloy during the baking treatment, and increases as the amount of solid solution of Si, Mg, Cu and the like increases, and is an index indicating the amount of solid solution. It is preferably limited to 0.3 μΩ · cm or more.
【００１５】製造条件について説明すると、本発明のア
ルミニウム合金は、例えば連続鋳造によって鋳塊とし、
鋳塊均質化処理を経て、常法に従って熱間圧延を行い、
所定の板厚まで冷間圧延した後、連続焼鈍炉で500 〜55
0 ℃に加熱する溶体化処理を行う。連続焼鈍炉は、金属
板コイルを巻き戻しながら連続的に加熱ゾーンを通過さ
せることにより加熱処理を行うもので、アルミニウム板
の焼鈍設備としてよく知られているものである。The production conditions will be described. The aluminum alloy of the present invention is made into an ingot by continuous casting, for example.
After ingot homogenization, hot rolling is performed according to the usual method,
After cold rolling to the specified thickness, 500-55 in a continuous annealing furnace
Perform a solution treatment by heating to 0 ° C. The continuous annealing furnace performs heat treatment by continuously passing a heating zone while rewinding a metal plate coil, and is well known as an aluminum plate annealing facility.
【００１６】連続焼鈍炉で溶体化処理することにより、
熱間圧延により析出したＭｇ2 Ｓｉ相やＡｌ−Ｃｕ−Ｍ
ｇ系化合物をマトリックス中に再固溶させ、これらを塗
装焼付処理で再析出させることによって加工組織の回復
を遅らせ、塗装焼付処理後の強度低下を少なくする。溶
体化処理は500 〜550 ℃に加熱することにより行われ
る。加熱温度が500 ℃未満ではＭｇ2 Ｓｉ相やＡｌ−Ｃ
ｕ−Ｍｇ系化合物の十分な再固溶が得られず、加熱温度
が550 ℃を越えると、合金中に形成されている共晶成分
（Ａｌ−Ｍｇ−Ｃｕ系化合物等）が融解して、焼鈍中や
最終冷間圧延において板に割れを生じるおそれがある。
溶体化処理温度に達するまでの昇温速度は特に規定する
必要はないが、溶体化処理温度からの冷却速度について
は10℃/s以上程度の冷却速度を維持するのがよい。冷却
速度が遅いと、冷却途中でＭｇ2 Ｓｉ相やＡｌ−Ｃｕ−
Ｍｇ系化合物が粗大に析出してしまい、塗装焼付処理時
これらの微細析出が少なくなるため、塗装焼付処理後の
強度低下が大きくなる。By performing a solution treatment in a continuous annealing furnace,
Mg 2 Si phase or Al-Cu-M precipitated by hot rolling
The g-based compound is re-dissolved in the matrix and reprecipitated by paint baking, thereby delaying the recovery of the processed structure and reducing a decrease in strength after the paint baking. The solution treatment is performed by heating to 500 to 550 ° C. If the heating temperature is lower than 500 ° C, Mg 2 Si phase or Al-C
If the u-Mg-based compound is not sufficiently re-dissolved and the heating temperature exceeds 550 ° C, the eutectic component (Al-Mg-Cu-based compound, etc.) formed in the alloy is melted, During annealing or during final cold rolling, the sheet may be cracked.
It is not necessary to particularly define the heating rate until the solution treatment temperature is reached, but the cooling rate from the solution treatment temperature is preferably maintained at about 10 ° C./s or more. If the cooling rate is low, the Mg 2 Si phase or Al-Cu-
Since the Mg-based compound is coarsely precipitated, and these fine precipitates are reduced during the coating baking treatment, the strength decrease after the coating baking treatment is increased.
【００１７】溶体化処理に続いて行われる最終冷間圧延
は、加工硬化により合金板材の強度を高め、塗装焼付処
理後の板材の強度を維持するために必要である。好まし
い圧延加工率は70〜85％であり、70％未満では、塗装焼
付処理、とくに２コート２ベークによる処理後の合金の
耐力を350 ＭＰａ以上にすることができない。冷間圧延
率が85％を越えると、板材の強度は上昇するが、転位が
堆積して板内部のひずみエネルギーが大きくなり過ぎ、
塗装焼付処理における加熱時に加工組織が回復し易くな
るため、塗装焼付処理後の耐力が350 ＭＰａ未満とな
る。また、冷間圧延中に板端部に割れが発生し易くな
る。The final cold rolling subsequent to the solution treatment is necessary for increasing the strength of the alloy sheet by work hardening and maintaining the strength of the sheet after the paint baking treatment. The preferred rolling reduction ratio is 70 to 85%, and if it is less than 70%, the yield strength of the alloy after the paint baking treatment, particularly the treatment by two coats and two bake, cannot be 350 MPa or more. When the cold rolling ratio exceeds 85%, the strength of the sheet increases, but dislocations accumulate and the strain energy inside the sheet becomes too large.
Since the processed structure is easily recovered at the time of heating in the paint baking treatment, the yield strength after the paint baking treatment is less than 350 MPa. In addition, cracks tend to occur at the end of the sheet during cold rolling.
【００１８】[0018]
【作用】本発明は上記の構成からなり、合金成分中のＳ
ｉ、Ｍｇ、ＭｎおよびＣｕの量を調整し、これらの元素
の相互作用により、塗装焼付処理時これらの元素間ある
いはこれらの元素とＡｌ間の金属間化合物を合金マトリ
ックス中に微細に析出させて、塗装焼付処理後の合金の
強度低下を抑え、Ｆｅ含有量を制限しＴｉを添加するこ
とにより、圧延板端部に割れを生じることなく高圧下冷
間圧延を可能として、合金の強度向上を図り、塗装焼付
処理に相当する230 ℃以下で50秒以上の加熱処理を行っ
た後において350 ＭＰａ以上の耐力を確保するものであ
る。The present invention has the above-mentioned structure and comprises S in the alloy component.
The amounts of i, Mg, Mn and Cu are adjusted, and the interaction of these elements causes the intermetallic compound between these elements or between these elements and Al to be finely precipitated in the alloy matrix during the coating baking treatment. By suppressing the decrease in the strength of the alloy after the paint baking treatment, limiting the Fe content and adding Ti, it is possible to perform cold rolling under high pressure without causing cracks at the end of the rolled sheet, thereby improving the strength of the alloy. As a result, a proof stress of 350 MPa or more is ensured after performing a heat treatment at 230 ° C. or less for 50 seconds or more, which is equivalent to a paint baking treatment.
【００１９】[0019]
【実施例】以下、本発明の実施例を比較例と対比して説
明する。 実施例１ 表１に示すアルミニウム合金を、常法により溶解、連続
鋳造により鋳塊とし、この鋳塊を500 ℃で8 時間均質化
処理後、板厚2.5mm まで熱間圧延した。なお、熱間圧延
の終了温度は290 〜330 ℃に調整した。ついで70％の加
工度で冷間圧延した後、連続焼鈍炉を使用して溶体化処
理を行った。溶体化処理は、昇温速度10℃/sで500 ℃ま
で上げ、この温度で10秒保持後冷却速度10℃/sで常温ま
で冷却する条件で行った。溶体化処理後の最終冷間圧延
加工率は80％とし、板厚0.15mmの試験材を得た。Hereinafter, examples of the present invention will be described in comparison with comparative examples. Example 1 An aluminum alloy shown in Table 1 was melted by a conventional method and formed into an ingot by continuous casting. The ingot was homogenized at 500 ° C. for 8 hours and then hot-rolled to a thickness of 2.5 mm. The hot rolling end temperature was adjusted to 290 to 330 ° C. Then, after cold rolling at a working ratio of 70%, a solution treatment was performed using a continuous annealing furnace. The solution treatment was performed under the conditions of raising the temperature to 500 ° C. at a rate of temperature rise of 10 ° C./s, holding at this temperature for 10 seconds, and then cooling to room temperature at a cooling rate of 10 ° C./s. The final cold rolling rate after the solution treatment was 80%, and a test material having a thickness of 0.15 mm was obtained.
【００２０】[0020]
【表１】 [Table 1]
【００２１】試験材について、圧延板両端部の割れ発生
の程度を目視で観察し、割れが検出されないものを○、
割れ長さが5mm 以下のものを△、割れ長さが5mm を越え
るものを×として評価した。また、引張試験を行って引
張強度、耐力、伸び率を測定すとともに、２コート２ベ
ークの塗装焼付処理を想定して、オイルバスを用いて試
験材を230 ℃で100 秒間加熱した後の試料についてJIS
5 号引張試験片により引張性能を測定し、当該加熱後の
耐力低下率を下記の式で評価した。 耐力低下率（％）＝（最終冷間圧延後耐力−加熱後の耐
力）／（最終冷間圧延後の耐力) ×100 さらに電気抵抗を、試験片の両端部に電流リード線をス
ポット溶接し、該リード線を直流電源および電流計に接
続し、同じく試験片の両端部に電圧リード線をスポット
溶接して、該リード線に電圧計を継ぎ、全体を液体窒素
中に浸漬して、電源から直流電流を流し電流値（Ｉ）お
よび電位差（Ｖ）を測定する直流四端子法により測定
し、次式により電気抵抗率を求めた。 電気抵抗率（ρ）＝Ｒ×Ｓ／ｌ、但し、Ｒ＝Ｖ／Ｉ、
Ｓ：試験片の断面積、ｌ：電圧端子間の距離 測定、評価結果を表２に示す。With respect to the test materials, the degree of occurrence of cracks at both ends of the rolled plate was visually observed.
Those with a crack length of 5 mm or less were rated as △, and those with a crack length exceeding 5 mm were rated as x. In addition, a tensile test was performed to measure tensile strength, proof stress, and elongation, and the sample was heated at 230 ° C for 100 seconds using an oil bath, assuming a 2-coat 2-bake baking treatment. About JIS
Tensile performance was measured with a No. 5 tensile test piece, and the proof stress reduction rate after the heating was evaluated by the following formula. Yield reduction rate (%) = (Yield strength after final cold rolling-Yield strength after heating) / (Yield strength after final cold rolling) x 100 Furthermore, electrical resistance is measured by spot welding current leads to both ends of the test piece. The lead wire was connected to a DC power supply and an ammeter, and a voltage lead wire was spot-welded to both ends of the test piece, and the voltmeter was connected to the lead wire. Was measured by a DC four-terminal method for measuring a current value (I) and a potential difference (V), and an electric resistivity was obtained by the following equation. Electric resistivity (ρ) = R × S / l, where R = V / I,
S: cross-sectional area of test piece, l: distance between voltage terminals Table 2 shows the measurement and evaluation results.
【００２２】[0022]
【表２】 [Table 2]
【００２３】表２に示されるように、本発明に従って作
製された試験材は、いずれも最終冷間圧延板材の端縁部
に割れの発生がなく、230 ℃で100 秒間加熱後の耐力は
352ＭＰａ以上で、加熱後の耐力の低下は9.7 ％以下と
良好な結果を示した。As shown in Table 2, none of the test materials produced according to the present invention had any cracks at the edges of the final cold-rolled sheet material, and the proof stress after heating at 230 ° C. for 100 seconds.
At 352 MPa or more, the decrease in proof stress after heating was 9.7% or less, showing good results.
【００２４】実施例２ 実施例１の試験材No.1、No.4、No.6について、表３に示
す条件で溶体化処理および最終冷間圧延を行い、実施例
１と同様の方法で諸性能を評価した。結果を表４に示
す。なお、溶体化処理材は、最終板厚が0.15mmとなるよ
う調整された板厚を有し、70％の冷間圧延加工を加えた
ものである。連続焼鈍炉における昇温速度は10℃/sとし
た。表４の結果に示されるように、本発明のアルミニウ
ム合金を使用し、本発明の条件に従って製造された試験
材（発明例No.10 〜15）は、いずれも最終冷間圧延板材
の端縁部に割れの発生がなく、230 ℃で100 秒間加熱後
の耐力は352 ＭＰａ以上で、耐力の低下率は9.6 ％以下
と良好な性能を示した。Example 2 For test materials No. 1, No. 4 and No. 6 of Example 1, solution treatment and final cold rolling were performed under the conditions shown in Table 3, and the same method as in Example 1 was used. Various performances were evaluated. Table 4 shows the results. The solution-treated material had a thickness adjusted to a final thickness of 0.15 mm, and was subjected to 70% cold rolling. The rate of temperature rise in the continuous annealing furnace was 10 ° C / s. As shown in the results of Table 4, the test materials (Invention Examples Nos. 10 to 15) manufactured using the aluminum alloy of the present invention and according to the conditions of the present invention were all the edges of the final cold-rolled sheet material. No cracks occurred in the part, and the proof stress after heating at 230 ° C. for 100 seconds was 352 MPa or more, and the reduction rate of the proof stress was 9.6% or less, indicating good performance.
【００２５】[0025]
【表３】 [Table 3]
【００２６】[0026]
【表４】 [Table 4]
【００２７】比較例１ 表５に示す組成を有するアルミニウム合金を、実施例１
と同様な方法で鋳造、均質化処理、熱間圧延、冷間圧
延、溶体化処理および最終冷間圧延し、板厚0.15mmの試
験材を作製した。これらの試験材について、実施例１と
同じ方法で諸性能を評価した。評価結果を表６に示す。
なお、表５において、本発明の成分限定を外れたものに
は下線を付した。Comparative Example 1 An aluminum alloy having a composition shown in Table 5 was used in Example 1.
Casting, homogenization, hot rolling, cold rolling, solution treatment, and final cold rolling were performed in the same manner as described above to produce a test material having a thickness of 0.15 mm. Various properties of these test materials were evaluated in the same manner as in Example 1. Table 6 shows the evaluation results.
In Table 5, those which are outside the component limits of the present invention are underlined.
【００２８】[0028]
【表５】 [Table 5]
【００２９】[0029]
【表６】 [Table 6]
【００３０】表６に示されるように、本発明の成分限定
を外れたアルミニウム合金による試験材では、最終冷間
圧延板材の板端部の割れ発生あるいは加熱後の耐力低下
が生じた。試験材 No.1 はＴｉ含有量が少なく、No.2は
Ｔｉ含有量が0.20％を越えるため、いずれも板端部に割
れが生じた。No.3はＳｉ量が少ないため加熱後の耐力の
低下が大きく、No.4はＳｉ量が限定範囲を越え、No.5は
Ｆｅ量が制限範囲を越えるため、いずれも板端部に割れ
が発生した。No.6はＭｎの含有量が少なく、またNo.8は
Ｍｇの含有量が少ないため、いずれも230 ℃加熱後の耐
力低下が大きく、No.7はＭｎ量が多く、またNo.9はＭｇ
量が多いため、最終冷間圧延時に板端部に割れが生じ
た。試験材 No.10は本発明の必須成分であるＴｉを含有
せず、またNo.11 はＣｕ量が限定範囲を越えるため、冷
間圧延時に割れが発生した。As shown in Table 6, in the test material of the present invention made of an aluminum alloy out of the composition limitation, cracks occurred at the end of the final cold-rolled sheet or the proof stress after heating occurred. Test material No. 1 had a low Ti content, and No. 2 had a Ti content exceeding 0.20%, so that cracks occurred at the plate edges in all cases. No.3 has a large decrease in yield strength after heating due to low Si content, No.4 has a Si content beyond the limited range, and No.5 has a Fe content outside the limited range, so all cracks at the plate edge There has occurred. No. 6 has a low Mn content, and No. 8 has a low Mg content, so that all have a large decrease in proof stress after heating at 230 ° C., No. 7 has a high Mn content, and No. 9 has a high Mn content. Mg
Due to the large amount, cracks occurred at the end of the sheet during the final cold rolling. Test material No. 10 did not contain Ti, which is an essential component of the present invention, and No. 11 cracked during cold rolling because the Cu content exceeded the limited range.
【００３１】比較例２ 実施例１で作製した試験材No.1、No.4、No.6について、
表７に示す条件で溶体化処理および最終冷間圧延加工を
行い、実施例１と同様な方法で諸性能を評価した。評価
結果を表８に示す。なお、溶体化処理材は、最終板厚が
0.15mmとなるよう調整された板厚を有し、70％の冷間圧
延を加えたものである。連続焼鈍炉での昇温速度は10℃
/s、バッチ炉の昇温速度は50℃/sとした。本発明の条件
を外れたものには下線を付した。Comparative Example 2 For the test materials No. 1, No. 4 and No. 6 prepared in Example 1,
Solution treatment and final cold rolling were performed under the conditions shown in Table 7, and various performances were evaluated in the same manner as in Example 1. Table 8 shows the evaluation results. The final thickness of the solution heat treated material is
It has a thickness adjusted to 0.15 mm and is 70% cold-rolled. Heating rate in continuous annealing furnace is 10 ℃
/ s, and the heating rate of the batch furnace was 50 ° C./s. Those outside the conditions of the present invention are underlined.
【００３２】[0032]
【表７】 [Table 7]
【００３３】[0033]
【表８】 [Table 8]
【００３４】表８に示されるように、本発明の条件を満
たさない溶体化処理あるいは最終冷間圧延を行って作製
した試験材では、耐力低下または板端部の割れが発生し
た。比較例No.12 、No.14 は、溶体化処理温度が低いた
め合金元素の再固溶が不十分となり、耐力低下が生じ
た。No.13 は、溶体化処理温度が高いため、一部に共晶
融解が生じ、最終冷間圧延時に板端部に割れが発生し
た。No.15 は、最終冷間圧延率が下限以下であるため十
分な加工硬化が得られず、加熱後の耐力が低い。試験材
No.16 は、最終冷間圧延率が限定範囲を越えているため
板端部に割れが生じ、同時に230 ℃での加熱処理におい
て加工組織が回復し易くなり、耐力の低下が大きくな
る。No.17 、No.18 、No.19 は、いずれも溶体化処理を
バッチ炉で行ったもので、230 ℃の加熱時にＭｇ2 Ｓｉ
相やＡｌ−Ｃｕ−Ｍｇ系化合物の微細析出を得るための
固溶状態が達成されないため、加熱後の耐力が低く、耐
力低下も大きい。As shown in Table 8, in the test materials produced by solution treatment or final cold rolling that did not satisfy the conditions of the present invention, a reduction in proof stress or cracks at the plate edge occurred. In Comparative Examples No. 12 and No. 14, since the solution treatment temperature was low, the re-solid solution of the alloy element was insufficient, and the proof stress was reduced. In No. 13, since the solution treatment temperature was high, eutectic melting occurred partially, and cracks occurred at the plate edge during the final cold rolling. In No. 15, sufficient work hardening was not obtained because the final cold rolling ratio was below the lower limit, and the proof stress after heating was low. Test material
In No. 16, since the final cold rolling reduction exceeds the limited range, cracks occur at the plate edge, and at the same time, the processed structure is easily recovered by heat treatment at 230 ° C., and the proof stress is greatly reduced. No. 17, No. 18 and No. 19 were all subjected to a solution treatment in a batch furnace, and the Mg 2 Si was heated at 230 ° C.
Since a solid solution state for obtaining fine phases or Al—Cu—Mg based compounds is not achieved, the yield strength after heating is low and the yield strength is large.
【００３５】[0035]
【発明の効果】本発明によれば、最終冷間加工性が高め
られ、塗装焼付処理による強度低下が少ないブラインド
用アルミニウム合金板材が提供される。冷間圧延加工に
おける１回当たりの圧下率も大きくできるから生産能率
も向上する。According to the present invention, there is provided an aluminum alloy sheet for blinds, which has improved final cold workability and has a small decrease in strength due to coating baking. Since the rolling reduction per cold rolling process can be increased, the production efficiency is also improved.
フロントページの続き (51)Int.Cl.6 識別記号 ＦＩ Ｃ２２Ｆ 1/00 ６７３ Ｃ２２Ｆ 1/00 ６７３ ６８５ ６８５Ｚ ６８６ ６８６Ａ ６９１ ６９１Ｂ ６９４ ６９４Ａ Continued on the front page (51) Int.Cl. 6 Identification code FI C22F 1/00 673 C22F 1/00 673 685 685Z 686 686A 691 691B 694 694A
Claims (2)
じ）、Ｍｇ０．５〜０．８％、Ｍｎ０．８〜１．２％、
Ｔｉ０．０５〜０．２０％およびＣｕ０．１〜０．３％
を含有し、不純物としてのＦｅを０．３０％以下に制限
し、残部Ａｌおよび不可避的不純物からなるアルミニウ
ム合金の冷間圧延板であって、耐力が４００ＭＰａ以
下、電気抵抗率が１．３μΩ・ｃｍ以上であり、２３０
℃以下で５０秒以上の塗装焼付処理を行った後における
耐力が３５０ＭＰａ以上であることを特徴とするブライ
ンド用アルミニウム合金板材。1. Si 1.0 to 1.5% (mass%, the same applies hereinafter), Mg 0.5 to 0.8%, Mn 0.8 to 1.2%,
Ti 0.05 to 0.20% and Cu 0.1 to 0.3%
, A cold-rolled plate of an aluminum alloy containing Al and unavoidable impurities with a proof stress of 400 MPa or less and an electric resistivity of 1.3 μΩ · cm or more and 230
An aluminum alloy sheet for blinds, which has a proof stress of 350 MPa or more after performing a coating baking treatment at 50 ° C. or less for 50 seconds or more.
Ｍｎ0.8 〜1.2 ％、Ｔｉ0.05〜0.20％およびＣｕ0.1 〜
0.3 ％を含有し、不純物としてのＦｅを0.30％以下に制
限し、残部Ａｌおよび不可避的不純物からなるアルミニ
ウム合金を、熱間圧延並びに冷間圧延し、連続焼鈍炉に
より500 〜550 ℃に加熱する溶体化処理を行った後、加
工率70〜85％で最終冷間圧延することを特徴とする、23
0 ℃以下で50秒以上の塗装焼付処理を行った後における
耐力が350 ＭＰａ以上であるブラインド用アルミニウム
合金板材の製造方法。(2) Si 1.0 to 1.5%, Mg 0.5 to 0.8%,
Mn 0.8-1.2%, Ti 0.05-0.20% and Cu 0.1-
An aluminum alloy containing 0.3%, Fe as an impurity is limited to 0.30% or less, and an aluminum alloy containing the balance of Al and inevitable impurities is hot-rolled and cold-rolled, and heated to 500 to 550 ° C. by a continuous annealing furnace. After solution treatment, final cold rolling is performed at a working ratio of 70 to 85%.
A method for producing an aluminum alloy sheet for blinds having a proof stress of 350 MPa or more after performing a coating baking treatment at 0 ° C. or less for 50 seconds or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5077703A JP2747770B2 (en) | 1993-03-11 | 1993-03-11 | Aluminum alloy sheet for blinds and method of manufacturing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5077703A JP2747770B2 (en) | 1993-03-11 | 1993-03-11 | Aluminum alloy sheet for blinds and method of manufacturing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH06264171A JPH06264171A (en) | 1994-09-20 |
| JP2747770B2 true JP2747770B2 (en) | 1998-05-06 |
Family
ID=13641266
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5077703A Expired - Fee Related JP2747770B2 (en) | 1993-03-11 | 1993-03-11 | Aluminum alloy sheet for blinds and method of manufacturing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2747770B2 (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE60203801T2 (en) * | 2001-07-09 | 2006-05-18 | Corus Aluminium Walzprodukte Gmbh | Weldable high strength Al-Mg-Si alloy |
| CA2450767C (en) * | 2001-07-23 | 2010-09-14 | Corus Aluminium Walzprodukte Gmbh | Weldable high strength al-mg-si alloy |
| PL3164524T3 (en) | 2014-07-04 | 2020-04-30 | Aleris Rolled Products Germany Gmbh | Aluminium alloy for use in the building industry |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01205050A (en) * | 1988-02-12 | 1989-08-17 | Furukawa Alum Co Ltd | Aluminum alloy material for blind |
| JPH0776411B2 (en) * | 1990-07-31 | 1995-08-16 | 株式会社神戸製鋼所 | Method for manufacturing thin-walled high-strength blind aluminum material |
| JPH04231434A (en) * | 1990-12-27 | 1992-08-20 | Furukawa Alum Co Ltd | Aluminum alloy for forming excellent in baking hardenability |
-
1993
- 1993-03-11 JP JP5077703A patent/JP2747770B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH06264171A (en) | 1994-09-20 |
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