JP2005163097A - HIGH STRENGTH Al-Fe ALLOY FOIL - Google Patents
HIGH STRENGTH Al-Fe ALLOY FOIL Download PDFInfo
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- JP2005163097A JP2005163097A JP2003402922A JP2003402922A JP2005163097A JP 2005163097 A JP2005163097 A JP 2005163097A JP 2003402922 A JP2003402922 A JP 2003402922A JP 2003402922 A JP2003402922 A JP 2003402922A JP 2005163097 A JP2005163097 A JP 2005163097A
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- 239000011888 foil Substances 0.000 title claims abstract description 36
- 229910018084 Al-Fe Inorganic materials 0.000 title claims abstract description 25
- 229910018192 Al—Fe Inorganic materials 0.000 title claims abstract description 25
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 22
- 239000000956 alloy Substances 0.000 title claims abstract description 22
- 229910000765 intermetallic Inorganic materials 0.000 claims abstract description 32
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 239000011159 matrix material Substances 0.000 claims abstract description 3
- 229910052782 aluminium Inorganic materials 0.000 claims description 7
- 229910052742 iron Inorganic materials 0.000 abstract description 2
- 229910052748 manganese Inorganic materials 0.000 abstract description 2
- 239000000203 mixture Substances 0.000 abstract description 2
- 238000000137 annealing Methods 0.000 description 30
- 238000005097 cold rolling Methods 0.000 description 15
- 238000005096 rolling process Methods 0.000 description 13
- 238000009826 distribution Methods 0.000 description 12
- 238000005098 hot rolling Methods 0.000 description 10
- 238000005266 casting Methods 0.000 description 8
- 239000013078 crystal Substances 0.000 description 6
- 230000000694 effects Effects 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 238000001556 precipitation Methods 0.000 description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 238000000265 homogenisation Methods 0.000 description 4
- 230000001105 regulatory effect Effects 0.000 description 4
- 238000004806 packaging method and process Methods 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 238000011084 recovery Methods 0.000 description 3
- 229910000838 Al alloy Inorganic materials 0.000 description 2
- 229910002551 Fe-Mn Inorganic materials 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 239000010419 fine particle Substances 0.000 description 2
- 230000007774 longterm Effects 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 229910018191 Al—Fe—Si Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 239000003814 drug Substances 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000000691 measurement method Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
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Abstract
Description
本発明は、高強度Ａｌ−Ｆｅ合金箔、詳しくは、強度に優れ、ピンホールや破断を生じることなしに薄肉化することができるＡｌ−Ｆｅ合金箔に関する。 The present invention relates to a high-strength Al—Fe alloy foil, and more particularly to an Al—Fe alloy foil that has excellent strength and can be thinned without causing pinholes or breakage.
食料品や薬品の包装などの用途に使用されるアルミニウム箔は、５〜２００μｍ程度の板厚を有するもので、アルミニウム箔が単独で使用されることは少なく、多くの場合、ポリエチレンなどと貼り合わせて使用される。 Aluminum foil used for food and medicine packaging has a plate thickness of about 5 to 200 μm, and aluminum foil is rarely used alone. Used.
このような用途のアルミニウム箔については、内容物を湿気や光から保護するために、ピンホールが少ないという特性をそなえることが重要であり、ピンホールは、箔厚が薄くなるに従い指数関数的に増加し、従来この種用途に使用されてきた純アルミニウム系の薄箔ではピンホールが多くなるため、薄箔用途には、ピンホールの少ないアルミニウム合金箔が要求され、その一つとしてピンホールの少ないＡｌ−Ｆｅ合金箔が提案されている。 In order to protect the contents of aluminum foil from moisture and light, it is important to have the property that there are few pinholes, and pinholes exponentially as the foil thickness decreases. Since the number of pinholes in the pure aluminum-based thin foil that has been used for this type of application has increased, an aluminum alloy foil with few pinholes is required for thin foil applications. Fewer Al-Fe alloy foils have been proposed.
例えば、Ｆｅ：０．８〜２．８％、Ｓｉ：０．０４〜０．２％を含有し、残部Ａｌと、不純物としてＣｕ含有量を０．００５％以下、Ｔｉ含有量を０．０３％以下、その他の不可避的不純物の含有量を合計で０．０５％以下に規制したＡｌ−Ｆｅ合金箔（特許文献１参照）が提案されている。このＡｌ−Ｆｅ合金箔においては、Ｆｅの大部分を金属間化合物としてアルミニウム母材中に分散させ、圧延中に導入される転位を均一に分散または回復させることにより、不均一な変形に起因するピンホール発生を低下させようとするものであるが、圧延中に導入される転位の分散または回復が容易であるため、圧延中の加工熱が不均一となった時には、局部的に先進率が変化して箔切れなどのトラブルが生じ易くなるという問題点がある。 For example, Fe: 0.8 to 2.8%, Si: 0.04 to 0.2% are contained, the balance is Al, and Cu content is 0.005% or less as impurities, and Ti content is 0.03. %, And an Al—Fe alloy foil in which the content of other inevitable impurities is regulated to 0.05% or less in total (see Patent Document 1) has been proposed. In this Al-Fe alloy foil, most of Fe is dispersed as an intermetallic compound in an aluminum base material, and dislocations introduced during rolling are uniformly dispersed or recovered, resulting in nonuniform deformation. Although it is intended to reduce the generation of pinholes, it is easy to disperse or recover the dislocations introduced during rolling, so when the processing heat during rolling becomes uneven, the advance rate is locally There is a problem in that troubles such as a foil breakage are likely to occur.
Ｆｅの一部を固溶させて転位の回復し易さを低減するアイデアもあり、過去において、Ｆｅ：０．８〜２．８％、Ｓｉ：０．２％以下、、残部Ａｌおよび不純物からなり、固溶Ｆｅ濃度を０．０２％以下に規制したＡｌ−Ｆｅ合金箔が提案されている（特許文献２参照）。このアイデアは高温均質化処理、高温中間焼鈍、長時間中間焼鈍などによりＦｅの一部を固溶させるもので、上記の提案のものにおいても、固溶Ｆｅ濃度の制御は鋳造から箔地焼鈍までの熱処理により行われ、例えば熱間圧延後３００〜４００℃で１０時間以上の焼鈍が行われるが、高温均質化処理、高温中間焼鈍、長時間中間焼鈍により１μｍ未満の微細な金属間化合物を多く固溶する結果、最終焼鈍時のピニング効果が低減して強度が低下するとともに、圧延中に不均一な変形が生じ易くなるためピンホールが発生し易くなるという難点がある。 There is also an idea to reduce the ease of dislocation recovery by dissolving a part of Fe, and in the past, Fe: 0.8 to 2.8%, Si: 0.2% or less, the remainder from Al and impurities Therefore, an Al—Fe alloy foil whose solid solution Fe concentration is regulated to 0.02% or less has been proposed (see Patent Document 2). This idea is to dissolve a part of Fe by high-temperature homogenization treatment, high-temperature intermediate annealing, long-term intermediate annealing, etc. Even in the above proposal, the control of the solid-solution Fe concentration is from casting to foil annealing. For example, after hot rolling, annealing is performed at 300 to 400 ° C. for 10 hours or more. However, high-temperature homogenization treatment, high-temperature intermediate annealing, and long-term intermediate annealing increase the amount of fine intermetallic compounds less than 1 μm. As a result of the solid solution, the pinning effect at the time of final annealing is reduced, the strength is lowered, and non-uniform deformation is likely to occur during rolling, so that pinholes are easily generated.
Ａｌ−Ｆｅ合金箔を溶湯圧延により製造する方法も提案されている（特許文献３参照）このものにおいては、Ｆｅが連続鋳造圧延時にＡｌ−Ｆｅ系金属間化合物として微細に晶出し、続く熱間圧延と冷間圧延により粉砕して０．２〜５μｍの大きさの微細粒子として均一に分散され、その結果、この微細粒子の周囲に箔圧延中に転位が局部的に堆積して、これを駆動力として動的回復が起こるため圧延硬化の進行が抑制されピンホールが少なくなるというものであるが、この方法では、金属間化合物の分布が不均一となり易く、薄箔圧延の際、部分的な加工軟化が生じて圧延切れが生じたり、溶湯圧延時に混入し易い酸化物に起因してピンホールが発生するという問題点がある。
発明者らは、上記従来のＡｌ−Ｆｅ合金箔における問題点を解消して、高強度でピンホールの少ないＡｌ−Ｆｅ合金箔を得るために、これらの特性と金属間化合物の分布形態との関連性について試験、検討を行った結果、０．２μｍ以上１．０μｍ未満の大きさの金属間化合物の分布密度を特定範囲とした場合にピンホールが低減され、強度に優れたＡｌ−Ｆｅ合金箔が得られることを見出した。 In order to solve the problems in the conventional Al-Fe alloy foil and to obtain an Al-Fe alloy foil with high strength and few pinholes, the inventors have determined the relationship between these characteristics and the distribution form of intermetallic compounds. As a result of examining and examining the relevance, when the distribution density of the intermetallic compound having a size of 0.2 μm or more and less than 1.0 μm is set within a specific range, pinholes are reduced and the Al—Fe alloy having excellent strength It was found that a foil was obtained.
本発明は、上記の知見に基づいてなされたものであり、その目的は、高強度でピンホールが少なく、包装用その他の用途に好適なＡｌ−Ｆｅ合金箔を提供することにある。 The present invention has been made based on the above findings, and an object of the present invention is to provide an Al—Fe alloy foil that is high in strength and has few pinholes and is suitable for other uses for packaging.
上記の目的を達成するための本発明による高強度Ａｌ−Ｆｅ合金箔は、Ｆｅ：０．８〜２．０％、Ｓｉを０．２％以下、Ｍｎを０．１％以下を含有し、残部Ａｌおよび不純物からなり、マトリックス中に円相当直径０．２〜１．０μｍの金属間化合物が４×１０6 〜８×１０6 個／ｃｍ2 分散していることを特徴とする。 The high-strength Al—Fe alloy foil according to the present invention for achieving the above object contains Fe: 0.8 to 2.0%, Si is 0.2% or less, and Mn is 0.1% or less. It consists of the balance Al and impurities, and is characterized in that 4 × 10 6 to 8 × 10 6 / cm 2 of intermetallic compounds having an equivalent circle diameter of 0.2 to 1.0 μm are dispersed in the matrix.
本発明によれば、高強度でピンホールが少なく、包装用その他の用途に好適なＡｌ−Ｆｅ合金箔を提供される。 ADVANTAGE OF THE INVENTION According to this invention, Al-Fe alloy foil with high intensity | strength and few pinholes and suitable for the other use for packaging is provided.
本発明における含有成分の意義および限定理由について説明すると、Ｆｅは強度を向上させるよう機能し、Ａｌ−Ｆｅ系の金属間化合物を形成する。Ｆｅの好ましい含有範囲は０．８〜２．０％であり、０．８％未満では、形成される金属間化合物数が少ないため、その効果が十分でなく、２．０％を越えると、粗大な金属間化合物が生成して機械的性質が低下し、ピンホールが生じ易くなる。Ｆｅのさらに好ましい含有範囲は１．２〜１．６％である。 The significance and reasons for limitation of the components contained in the present invention will be described. Fe functions to improve strength and forms an Al—Fe-based intermetallic compound. The preferable content range of Fe is 0.8 to 2.0%, and if it is less than 0.8%, the number of intermetallic compounds formed is small, so that the effect is not sufficient, and if it exceeds 2.0%, Coarse intermetallic compounds are formed, the mechanical properties are lowered, and pinholes are easily generated. The more preferable content range of Fe is 1.2 to 1.6%.
Ｓｉは０．２％以下に規制することが好ましい。０．２％を越えて含有すると、鋳造時にＡｌ−Ｆｅ−Ｓｉ系の金属間化合物を生成し、この金属間化合物は球体であり、ピンホールを発生させ易くする。また、固溶Ｓｉは圧延中に不均一変形を引き起こし易くし、ピンホールを生じる。Ｓｉのさらに好ましい含有範囲は０．１％以下である。 Si is preferably regulated to 0.2% or less. If the content exceeds 0.2%, an Al—Fe—Si intermetallic compound is produced during casting, and the intermetallic compound is a sphere, which easily causes pinholes. Further, solute Si tends to cause non-uniform deformation during rolling, resulting in pinholes. A more preferable content range of Si is 0.1% or less.
Ｍｎは０．１％以下に規制することが好ましい。Ｍｎが０．１％以下の範囲で含有されると、Ａｌ−Ｆｅ系の金属間化合物の一部を置換して微細なＡｌ−Ｆｅ−Ｍｎ系の金属間化合物を形成し、最終焼鈍箔の強度が向上する。０．１％を越えると、粗大なＡｌ−Ｆｅ−Ｍｎ系の金属間化合物が形成し易くなってピンホールが増加するとともに、固溶したＭｎが最終焼鈍時に析出して、最終製品の結晶粒が粗大化し易くなる。Ｍｎのさらに好ましい含有範囲は０．０１〜０．０５％である。 Mn is preferably regulated to 0.1% or less. When Mn is contained in a range of 0.1% or less, a part of the Al-Fe-based intermetallic compound is substituted to form a fine Al-Fe-Mn-based intermetallic compound, and the final annealed foil Strength is improved. If it exceeds 0.1%, a coarse Al—Fe—Mn intermetallic compound is easily formed to increase pinholes, and solid solution Mn precipitates during final annealing, resulting in crystal grains of the final product. Tends to be coarsened. The more preferable content range of Mn is 0.01 to 0.05%.
本発明のＡｌ−Ｆｅ合金箔においては、その他の成分として、０．１％以下のＴｉ、０．１％以下のＢが含有されていても本発明の効果に影響することはなく、その他、Ｃｕ、Ｍｇ、Ｃｒ、Ｚｎなどの不純物は総量で０．２５％以下の範囲で許容される。 In the Al-Fe alloy foil of the present invention, even if 0.1% or less of Ti and 0.1% or less of B are contained as other components, the effect of the present invention is not affected. Impurities such as Cu, Mg, Cr and Zn are allowed in a total amount of 0.25% or less.
本発明においては、円相当直径が０．２〜１．０μｍの金属間化合物の分布数を特定範囲とすることにより、最終焼鈍時に結晶粒界移動が阻止され、結晶粒が微細化されて強度が向上する。上記金属間化合物の好ましい分布密度は４×１０6 〜８×１０6 個／ｃｍ2 の範囲であり、分布密度が４×１０6 個／ｃｍ2 未満では、転位が金属間化合物を乗り越えて移動するため強度向上の効果が小さく、分布密度が８×１０6 個／ｃｍ2 より大きいと、固溶成分が著しく低下するため、粗大な結晶粒が不均一に形成し、不均一結晶粒に起因する不均一変形によりピンホールが生じ易くなる。 In the present invention, by setting the number of distributions of intermetallic compounds having an equivalent circle diameter of 0.2 to 1.0 μm within a specific range, movement of crystal grain boundaries is prevented during final annealing, and crystal grains are refined and strength is increased. Will improve. The preferable distribution density of the intermetallic compound is in the range of 4 × 10 6 to 8 × 10 6 pieces / cm 2. When the distribution density is less than 4 × 10 6 pieces / cm 2 , the dislocation moves over the intermetallic compound. Therefore, if the distribution density is larger than 8 × 10 6 particles / cm 2 , the solid solution component is remarkably lowered, so that coarse crystal grains are formed unevenly, resulting in nonuniform crystal grains. Pinholes are likely to occur due to uneven deformation.
また、金属間化合物が０．２μｍより小さいと、転位または結晶粒界の移動を阻止する効果が小さく、金属間化合物が１．０μｍより大きいと、金属間化合物の周囲で回復が生じ易いため、加工軟化が促進され強度が低下する。 Also, if the intermetallic compound is smaller than 0.2 μm, the effect of preventing the movement of dislocations or crystal grain boundaries is small, and if the intermetallic compound is larger than 1.0 μm, recovery tends to occur around the intermetallic compound. Work softening is promoted and strength decreases.
金属間化合物の測定は、試料箔を電解研磨し、研磨後の表面を光学顕微鏡で４００倍に拡大した写真を撮影し、金属間化合物の粒径分布を画像解析装置（株式会社ニレコ製ルーゼックス５００）を用いて測定する。この場合、金属間化合物の直径は、円相当直径、すなわち、写真における金属間化合物の面積と同じ面積を有する円の直径として換算し、この結果から金属間化合物の粒径および数を測定する。 The intermetallic compound was measured by electrolytically polishing the sample foil, taking a photograph of the polished surface magnified 400 times with an optical microscope, and measuring the particle size distribution of the intermetallic compound with an image analyzer (Lusex 500 manufactured by Nireco Corporation). ) To measure. In this case, the diameter of the intermetallic compound is converted as the equivalent circle diameter, that is, the diameter of a circle having the same area as the area of the intermetallic compound in the photograph, and the particle diameter and number of the intermetallic compound are measured from the result.
本発明のＡｌ−Ｆｅ合金箔は、前記の組成を有するアルミニウム合金を、例えばＤＣ鋳造により造塊し、得られた鋳塊を均質化処理後、熱間圧延し、その後、２回の中間焼鈍を介しての冷間圧延を行うことにより製造され、最終焼鈍を施す。 The Al-Fe alloy foil of the present invention is an ingot of an aluminum alloy having the above composition, for example, by DC casting. The obtained ingot is homogenized and hot-rolled, and then subjected to two intermediate annealings. It is manufactured by carrying out cold rolling through a final annealing.
金属間化合物の分布密度の制御は、鋳造速度などの鋳造条件、均質化処理条件、熱間圧延条件、中間焼鈍条件、あるいはこれらの条件の組み合わせを調整することにより行われるが、上記の範囲の金属間化合物の分布密度を得るためには、鋳造速度を３５〜５０ｍｍ／分、均質化処理温度を４６０〜５００℃とするのが好ましい。また、熱間圧延後、加工度４０〜６０％の冷間圧延を行って析出サイトとなる加工歪を導入したのち第１回目の中間焼鈍を行い、その後冷間圧延し第２回目の中間焼鈍を施して、さらに冷間圧延するのが望ましく、第１〜２回目の中間焼鈍条件は３００〜４００℃で１〜５時間とするのが好ましい。 The distribution density of the intermetallic compound is controlled by adjusting casting conditions such as casting speed, homogenization treatment conditions, hot rolling conditions, intermediate annealing conditions, or a combination of these conditions. In order to obtain the distribution density of the intermetallic compound, it is preferable that the casting speed is 35 to 50 mm / min and the homogenization temperature is 460 to 500 ° C. In addition, after hot rolling, cold rolling at a work degree of 40 to 60% is performed to introduce a working strain that becomes a precipitation site, and then the first intermediate annealing is performed, and then cold rolling is performed and the second intermediate annealing is performed. It is desirable to further cold-roll, and the first and second intermediate annealing conditions are preferably 300 to 400 ° C. and 1 to 5 hours.
熱間圧延後の熱延コイルは析出または組織が不均一で、そのまま冷間圧延を行うと、不均一な析出が生じ易く、また組織の均一化も得られ難いため、そのまま冷間圧延を継続すると不均一組織部でピンホールが生じ易くなる。本発明においては、熱間圧延後、加工度４０〜６０％の冷間圧延を行い、その後中間焼鈍を行う。熱間圧延後できるだけ早く冷間圧延し、中間焼鈍を行うのが好ましい。熱間圧延後６０％を越える冷間圧延を施して中間焼鈍すると、形成された不均一な冷間圧延組織が均一化し難い。熱間圧延後、加工度４０〜６０％の冷間圧延を行い、その後第１回目の中間焼鈍を施して冷間圧延を行い、第２回目の中間焼鈍を施して、さらに冷間圧延することによって、析出量が多く、加工により転位が均一に導入されているため析出形態も微細且つ均一となる。熱間圧延後直ちに中間焼鈍を行っても加工組織が十分に導入されないため析出が促進されず、上記の効果が得難くなる。 The hot-rolled coil after hot rolling has a non-uniform precipitation or structure. If cold rolling is performed as it is, non-uniform precipitation is likely to occur and it is difficult to obtain a uniform structure. As a result, pinholes are likely to occur in the non-uniform tissue portion. In the present invention, after hot rolling, cold rolling with a work degree of 40 to 60% is performed, and then intermediate annealing is performed. It is preferable to cold-roll as soon as possible after hot rolling and to perform intermediate annealing. When cold rolling exceeding 60% is performed after hot rolling and intermediate annealing is performed, the formed non-uniform cold rolling structure is difficult to homogenize. After hot rolling, perform cold rolling with a workability of 40 to 60%, then perform the first intermediate annealing, perform cold rolling, perform the second intermediate annealing, and further cold rolling Therefore, the amount of precipitation is large, and dislocations are introduced uniformly by processing, so that the precipitation form is also fine and uniform. Even if the intermediate annealing is performed immediately after the hot rolling, the processed structure is not sufficiently introduced, so that the precipitation is not promoted and the above effect is difficult to obtain.
以下、本発明の実施例を比較例と対比して説明するとともに、それに基づいてその効果を実証する。なお、これらの実施例は本発明の好ましい一実施態様を示すものであり、本発明はこれに限定されるものではない。 Examples of the present invention will be described below in comparison with comparative examples, and the effects will be demonstrated based on the examples. These examples show one preferred embodiment of the present invention, and the present invention is not limited thereto.
Ｆｅ：１．２５％、Ｓｉ：０．０５％、Ｍｎ：０．０５％、不純物総量０．１７％を含有し、残部ＡｌからなるＡｌ−Ｆｅ合金を表１に示す鋳造速度でＤＣ鋳造により造塊し、得られた鋳塊を、表１に示す条件で均質化処理した。 An Al—Fe alloy containing Fe: 1.25%, Si: 0.05%, Mn: 0.05%, and a total amount of impurities of 0.17%, and the balance being Al is obtained by DC casting at a casting speed shown in Table 1. The ingot was obtained and homogenized with the conditions shown in Table 1.
ついで、熱間圧延により厚さ４ｍｍの熱延板とした後、熱延板を中間焼鈍を行うことなく加工度５０％の冷間圧延を行って、第１回目の中間焼鈍を行い、続いて冷間圧延（厚さ０．５ｍｍまで）−第２回目の中間焼鈍−冷間圧延により厚さ６μｍまで製箔（試験材Ｎｏ．１〜３及び５）し、３００℃の温度で最終焼鈍してＡｌ−Ｆｅ合金箔とした。中間焼鈍条件を表１に示す。試験材Ｎｏ．４は、熱延板（厚さ４ｍｍ）を厚さ０．５ｍｍまで冷間圧延した後、表１に示す条件で中間焼鈍し、ついで冷間圧延により厚さ６ｍｍまで製箔した。また試験材Ｎｏ．５は、熱延板（厚さ４ｍｍ）を３２５℃で１２時間中間焼鈍し、その後、中間焼鈍を行うことなしに冷間圧延を続行し厚さ６ｍｍまで製箔した。 Then, after hot rolling to obtain a hot rolled sheet having a thickness of 4 mm, the hot rolled sheet is subjected to cold rolling at a workability of 50% without performing intermediate annealing, and then the first intermediate annealing is performed. Cold rolling (up to 0.5 mm thickness)-Second intermediate annealing-Folding to 6 μm thickness by cold rolling (test materials No. 1 to 3 and 5) and final annealing at a temperature of 300 ° C Al-Fe alloy foil. Table 1 shows the intermediate annealing conditions. Test material No. In No. 4, a hot-rolled sheet (thickness 4 mm) was cold-rolled to a thickness of 0.5 mm, then subjected to intermediate annealing under the conditions shown in Table 1, and then cold-rolled to form a foil to a thickness of 6 mm. In addition, the test material No. In No. 5, hot-rolled sheets (thickness 4 mm) were subjected to intermediate annealing at 325 ° C. for 12 hours, and then cold rolling was continued without intermediate annealing to produce a foil having a thickness of 6 mm.
得られた最終焼鈍後のＡｌ−Ｆｅ合金箔について、前記の測定方法に従って０．２〜１．０μｍの金属間化合物の分布密度を測定し、最終焼鈍後の引張強さ、ピンホール数を測定した。結果を表２に示す。表２に示すように、本発明に従う試験材Ｎｏ．１〜３はいずれも、引張強さが１００ＭＰａを越える高強度を有し、ピンホール数もきわめて少ない。これに対して、金属間化合物の分布密度が本発明の条件を外れた試験材Ｎｏ．４〜６は、強度が低く、ピンホール数も多かった。 About the obtained Al-Fe alloy foil after the final annealing, the distribution density of the intermetallic compound of 0.2 to 1.0 μm is measured according to the above measurement method, and the tensile strength and the number of pinholes after the final annealing are measured. did. The results are shown in Table 2. As shown in Table 2, the test material No. 1-3 each have a high strength with a tensile strength exceeding 100 MPa, and the number of pinholes is extremely small. On the other hand, the test material No. in which the distribution density of the intermetallic compound deviates from the conditions of the present invention. 4 to 6 had low strength and a large number of pinholes.
Claims (1)
Fe: 0.8 to 2.0% (mass%, the same applies hereinafter), Si 0.2% or lower (including 0%, same hereafter), Mn 0.1% or lower (including 0%, hereafter the same) ), The balance consisting of Al and impurities, and an intermetallic compound having a circle-equivalent diameter of 0.2 to 1.0 μm dispersed in the matrix at 4 × 10 6 to 8 × 10 6 / cm 2 High strength Al-Fe alloy foil.
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| JP2007092150A (en) * | 2005-09-29 | 2007-04-12 | Dowa Holdings Co Ltd | Aluminum-ceramic joined substrate and method for producing the same |
| WO2014021170A1 (en) | 2012-08-01 | 2014-02-06 | 古河スカイ株式会社 | Aluminum alloy foil and method for producing same |
| JP2014101559A (en) * | 2012-11-21 | 2014-06-05 | Uacj Corp | Aluminum alloy foil, molding package material, battery, medicine packaging container and method of manufacturing aluminum alloy foil |
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| JP2007092150A (en) * | 2005-09-29 | 2007-04-12 | Dowa Holdings Co Ltd | Aluminum-ceramic joined substrate and method for producing the same |
| WO2014021170A1 (en) | 2012-08-01 | 2014-02-06 | 古河スカイ株式会社 | Aluminum alloy foil and method for producing same |
| KR20150034290A (en) | 2012-08-01 | 2015-04-02 | 가부시키가이샤 유에이씨제이 | Aluminum alloy foil and method for producing same |
| US9732402B2 (en) | 2012-08-01 | 2017-08-15 | Uacj Corporation | Aluminum alloy foil and method for manufacturing same |
| JP2014101559A (en) * | 2012-11-21 | 2014-06-05 | Uacj Corp | Aluminum alloy foil, molding package material, battery, medicine packaging container and method of manufacturing aluminum alloy foil |
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