WO2012117627A1 - Aluminum alloy foil for lithium ion battery electrode current collectors, and method for producing same - Google Patents
Aluminum alloy foil for lithium ion battery electrode current collectors, and method for producing same Download PDFInfo
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- WO2012117627A1 WO2012117627A1 PCT/JP2011/077000 JP2011077000W WO2012117627A1 WO 2012117627 A1 WO2012117627 A1 WO 2012117627A1 JP 2011077000 W JP2011077000 W JP 2011077000W WO 2012117627 A1 WO2012117627 A1 WO 2012117627A1
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- 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
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- 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
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M4/00—Electrodes
- H01M4/02—Electrodes composed of, or comprising, active material
- H01M4/64—Carriers or collectors
- H01M4/66—Selection of materials
- H01M4/661—Metal or alloys, e.g. alloy coatings
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M10/00—Secondary cells; Manufacture thereof
- H01M10/05—Accumulators with non-aqueous electrolyte
- H01M10/052—Li-accumulators
- H01M10/0525—Rocking-chair batteries, i.e. batteries with lithium insertion or intercalation in both electrodes; Lithium-ion batteries
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/10—Energy storage using batteries
Definitions
- the present invention is a high-strength and highly conductive lithium ion suitably used for an electrode current collector of a lithium ion secondary battery (hereinafter simply referred to as a lithium ion battery) used in a mobile phone, a notebook personal computer, etc.
- the present invention relates to an aluminum alloy foil for a battery electrode current collector and a method for producing the same.
- the lithium ion battery electrode current collector is composed of an electrode plate group in which a positive electrode and a negative electrode are wound with a separator interposed therebetween, and this is inserted into a battery case.
- the battery case has a cylindrical shape and a square shape, and a current collector is prepared according to the shape of the case. After inserting the current collector, a non-aqueous electrolyte is injected and sealed.
- the positive electrode active material lithium cobaltate, a lithium nickel composite compound or the like is used, and as the negative electrode active material, a carbon material capable of adsorbing and desorbing lithium ions such as coke and graphite is used.
- These positive electrode active materials or negative electrode active materials are stirred and mixed with a binder using polyvinylidene fluoride, etc., applied to the aluminum foil of the positive electrode or the copper foil of the negative electrode, dried and rolled, and heat-treated during or before and after rolling.
- Patent Document 1 To improve the adsorptive power, cut into a predetermined size and formed into a sheet shape, and used as an electrode of a lithium ion secondary battery.
- the aluminum foil for the positive electrode current collector in order to suppress the softening and strength reduction of the aluminum foil by heating in the drying process after the application of the positive electrode active material, and to prevent deformation of the aluminum foil in the rolling process, Mn and Cu are used.
- the contained aluminum alloy foil is used (Patent Document 2).
- JP 2007-234277 A Japanese Patent Laid-Open No. 11-67220
- the present invention has been made as a result of repeated tests and studies on the relationship between the component composition, strength, electrical resistance and battery characteristics in order to solve the above-described conventional problems in the aluminum foil for a positive electrode current collector of a lithium ion battery. It is an object of the present invention to provide an aluminum alloy foil for a lithium ion battery electrode current collector that exhibits higher strength and lower electrical resistance than conventional materials, and a method for producing the same.
- an aluminum alloy foil for a lithium ion battery electrode current collector has Mn: 0.4% (mass%, the same applies hereinafter) to less than 0.8%, Mg: 0.3 %: 0.8% or less, Si: 0.4% or less (excluding 0%, the same shall apply hereinafter), Fe: 0.8% or less, Ti: 0.05% or less, Mn and Mg contained It satisfies the relationship of Mn% + 4 ⁇ Mg% ⁇ 3.2% with respect to the amount, has a composition composed of the balance Al and inevitable impurities, has a tensile strength of 300 MPa or more, and a specific resistance value at room temperature of 3.7 ⁇ cm or less It is characterized by being.
- the aluminum alloy foil for a lithium ion battery electrode current collector according to claim 2 is characterized in that in claim 1, the aluminum alloy foil further contains Cu: 0.02% to 0.3%.
- a method for producing an aluminum alloy foil for a lithium ion battery electrode current collector according to claim 3 is a method for producing an aluminum alloy foil according to claim 1 or 2, wherein the composition according to claim 1 or 2 is used.
- An ingot of an aluminum alloy having an aluminum alloy is homogenized according to a conventional method, then subjected to hot rolling and cold rolling, and a final cold rolling reduction rate after performing an intermediate heat treatment with recrystallization in the cold rolling is 85%. It is the above.
- an aluminum alloy foil for a lithium ion battery electrode current collector that is particularly suitable for a positive electrode material.
- the aluminum alloy foil does not cause a decrease in strength even when heated in the drying process at the time of manufacturing the positive electrode plate, and has sufficient strength not to be deformed even in the rolling process, and also has a sufficiently low electrical resistance. High density and high energy can be achieved.
- Mn The dissolved Mn functions to improve the strength of the foil. Moreover, although the strength fall in the drying process at the time of positive electrode plate manufacture is suppressed, since solid solution Mn raises a specific resistance, it is desirable that there is little content from an electroconductive viewpoint.
- the preferable content of Mn is in the range of 0.4% or more and less than 0.8%. If the content is less than 0.4%, sufficient strength cannot be obtained. Since the value exceeds 3.7 ⁇ cm, it is not preferable. A more preferable content range of Mn is 0.5% or more and 0.7% or less.
- Mg functions to improve the strength together with Mn, and the specific resistance increases with the addition of Mg.
- the preferable content of Mg is in the range of 0.3% to 0.8%, and if it is less than 0.3%, the strength is insufficient.
- a more preferable content range of Mg is 0.4% or more and 0.7% or less.
- the specific resistance of the aluminum alloy foil is required to be 3.7 ⁇ cm or less.
- Mg the influence of Mg on the specific resistance
- the relationship between the Mg content and the Mn content must satisfy the following formula. Mn% + 4 ⁇ Mg% ⁇ 3.2%
- Si forms an Al—Mn—Si based compound during homogenization treatment or hot rolling, and reduces the solid solution amount of Mn.
- a preferable content of Si is 0.4% or less. In order to keep the amount of Si even lower, it is necessary to use high purity bullion, which increases costs.
- a more preferable content range of Si considering both cost and performance is 0.15% or more and 0.35% or less.
- Fe forms an Al—Mn—Fe-based compound at the time of casting, and reduces the solid solution amount of Mn.
- Al—Mn—Fe based compounds have a size of about 1 to 10 ⁇ m and do not contribute to strength. If the Fe content exceeds 0.8%, the solid solution amount of Mn decreases, and a predetermined strength cannot be obtained.
- coarse Al—Mn—Fe-based crystals are easily formed during casting, causing pinholes during foil rolling. In order to prevent the formation of coarse crystals, it is necessary to adjust the blending amount so that (Fe% + Mn%) is 1.4% or less in consideration of the addition of Mg. In order to keep the amount of Fe low, it is necessary to use high-purity bullion, which increases costs. Therefore, a more preferable range of Fe in consideration of both cost and performance is 0.4% or more and 0.7% or less. .
- Ti is added to refine the ingot structure. Ti increases the specific resistance even in a small amount, but if it exceeds 0.05%, it may cause pinholes during foil rolling. The same effect can be obtained by adding B together with Ti. For the same reason, the content of B in the aluminum alloy foil is preferably 0.01% or less.
- Cu functions to improve strength.
- the preferable content of Cu is in the range of 0.02% to 0.3%, and if it is less than 0.02%, the strength improvement effect is not sufficient.
- Cu has less influence on the increase in specific resistance than Mn, but if it exceeds 0.3%, the strength increases but the specific resistance also increases, which is not preferable. In addition, cracks are likely to occur during casting, making it difficult to manufacture on a mass production scale.
- a more preferable content range of Cu is 0.03% or more and 0.15% or less.
- Zn 0.1% or less, Cr, Ni, Ga, V, and other elements individually 0.05% or less, if the total is 0.15% or less, the characteristics of the present invention are affected. None do.
- the tensile strength has a sufficient strength of 300 MPa or more in order to prevent deformation in the rolling process.
- the manufacturing process of the aluminum alloy foil of the present invention will be described.
- the aluminum alloy having the above composition is melted and cast to form a predetermined slab, and the obtained slab (ingot) is homogenized according to a conventional method, followed by hot rolling.
- a lithium ion battery electrode current collector it is necessary to finish the foil material with a thickness of 20 ⁇ m or less, and cold rolling to such a thin foil without performing an intermediate heat treatment from a hot rolled plate is due to work hardening. Difficult for mass production due to increased strength. Therefore, cold rolling is performed by performing an intermediate heat treatment accompanied by recrystallization during rolling. In this case, in order to obtain a predetermined strength, it is necessary to set the final cold rolling rate after performing the intermediate heat treatment accompanied by recrystallization in cold rolling to 85% or more.
- Example 1 Aluminum alloys (A to K) having the composition shown in Table 1 were melted and ingot-formed by a semi-continuous casting method, and the resulting ingot was homogenized at a temperature of 480 ° C. for 5 hours, and then a temperature of 450 to 260 ° C. Hot rolling was performed in the range to obtain a hot rolled plate having a thickness of 3 mm. After cold-rolling the hot-rolled sheet to a thickness of 0.5 mm, an intermediate heat treatment is performed using a rapid heating furnace at a temperature of 400 ° C. for 1 minute and cooling at a cooling rate of 20 ° C./s After the heat treatment, cold rolling was repeated to obtain 15 ⁇ m aluminum alloy foils (test materials 1 to 11). The cold rolling rate at this time was 97%. In addition, about the conventional material (test material 11) (alloy: 3003 alloy), the foil material was created in the same process except performing the homogenization process for 5 hours at the temperature of 600 degreeC.
- the test materials 1 to 5 according to the present invention have a tensile strength of 300 MPa or more and a specific resistance at room temperature of 3.7 ⁇ cm or less, which is higher than that of the conventional material (test material 11) 3003 alloy foil. The strength is high and the specific resistance is reduced.
- test materials 6 to 10 outside the conditions of the present invention were inferior in either tensile strength or specific resistance. That is, since the test material 6 had a large amount of Mn, the specific resistance was high. Since the test material 7 had (Mn% + 4 ⁇ Mg%) larger than 3.2%, the specific resistance value was high.
- the test material 8 had a small amount of Mn, the tensile strength was less than 300 MPa.
- the test material 9 had a large amount of Fe, and an Al—Mn—Fe-based compound was produced during casting to reduce the solid solution amount of Mn. Therefore, the tensile strength was less than 300 MPa.
- the test material 10 had a large amount of Si and a decreased amount of Mn solid solution, and the amount of Mg was small, the tensile strength was less than 300 MPa.
- the test material 11 shows the characteristics of a conventional 3003 alloy foil, the tensile strength is less than 300 MPa, and the specific resistance exceeds 3.7 ⁇ cm.
- Example 2 Using alloy E ingoted in Example 1, homogenization treatment, hot rolling and cold rolling were performed under the same conditions as in the production of test materials 1 to 10 in Example 1, and only the final cold rolling rate was changed. An aluminum alloy foil having a thickness of 15 ⁇ m was manufactured, and the obtained alloy foil (test material) was measured for tensile properties and specific resistance at room temperature (25 ° C.) in the same manner as in Example 1. The results are shown in Table 3.
- test materials 12 to 14 according to the present invention exhibited characteristics of a tensile strength of 300 MPa or more and a specific resistance at room temperature of 3.7 ⁇ cm or less.
- test materials 15 to 17 had a tensile strength lower than 300 MPa because the final cold rolling rate was less than 85%.
Abstract
Provided is an aluminum alloy foil for lithium ion battery electrode current collectors that exhibits high strength and low electrical resistance, and is characterized by: having a composition containing Mn in the amount of 0.4% or more and less than 0.8%, Mg in the amount of 0.3% or more and 0.8% or less, Si in the amount of 0.4% or less, Fe in the amount of 0.8% or less, and Ti in the amount of 0.5% or less, satisfying a relationship (Mn%+4xMg%≤3.2%) pertaining to the amounts of Mn and Mg contained therein, and having Al and inevitable impurities constitute the remainder thereof; the tensile strength thereof being 300MPa or greater; and the specific resistance value thereof at room temperature being 3.7μΩcm or less.
Description
本発明は携帯電話やノート型パーソナルコンピューター等に利用されるリチウムイオン二次電池（以下、単にリチウムイオン電池）の電極集電体用として好適に使用される高強度で導電性に優れたリチウムイオン電池電極集電体用アルミニウム合金箔およびその製造方法に関する。
The present invention is a high-strength and highly conductive lithium ion suitably used for an electrode current collector of a lithium ion secondary battery (hereinafter simply referred to as a lithium ion battery) used in a mobile phone, a notebook personal computer, etc. The present invention relates to an aluminum alloy foil for a battery electrode current collector and a method for producing the same.
リチウムイオン電池電極集電体は、正極と負極がセパレータを介して捲回された極板群からなり、これを電池ケース内へ挿入する。電池ケースの形状としては円筒型と角型があり、ケースの形状にあわせて集電体を調製する。集電体を挿入後、非水電解液を注入して封口する。
The lithium ion battery electrode current collector is composed of an electrode plate group in which a positive electrode and a negative electrode are wound with a separator interposed therebetween, and this is inserted into a battery case. The battery case has a cylindrical shape and a square shape, and a current collector is prepared according to the shape of the case. After inserting the current collector, a non-aqueous electrolyte is injected and sealed.
正極活物質にはコバルト酸リチウム、リチウムニッケル複合化合物などが用いられ、負極活物質としてはコークスや黒鉛等のリチウムイオンを吸脱着できる炭素材料が用いられている。これらの正極活物質または負極活物質はポリフッ化ビニリデン等を使用したバインダーと撹拌・混合し、正極のアルミ箔や負極の銅箔に塗布して乾燥後圧延を行い、圧延中もしくは圧延前後で熱処理を行って吸着力を向上させ、所定寸法に裁断してシート状に成形し、リチウムイオン二次電池の電極とする（特許文献１）。
As the positive electrode active material, lithium cobaltate, a lithium nickel composite compound or the like is used, and as the negative electrode active material, a carbon material capable of adsorbing and desorbing lithium ions such as coke and graphite is used. These positive electrode active materials or negative electrode active materials are stirred and mixed with a binder using polyvinylidene fluoride, etc., applied to the aluminum foil of the positive electrode or the copper foil of the negative electrode, dried and rolled, and heat-treated during or before and after rolling. To improve the adsorptive power, cut into a predetermined size and formed into a sheet shape, and used as an electrode of a lithium ion secondary battery (Patent Document 1).
正極集電体用アルミニウム箔に関しては、正極活物質塗布後の乾燥工程での加熱によるアルミニウム箔の軟化、強度低下を抑制し、圧延工程におけるアルミニウム箔の変形を防止するために、ＭｎやＣｕを含有したアルミニウム合金箔が用いられている（特許文献２）。
Regarding the aluminum foil for the positive electrode current collector, in order to suppress the softening and strength reduction of the aluminum foil by heating in the drying process after the application of the positive electrode active material, and to prevent deformation of the aluminum foil in the rolling process, Mn and Cu are used. The contained aluminum alloy foil is used (Patent Document 2).
近年、リチウムイオン電池の一層の高密度高エネルギー化が要求されており、従来から正極集電体として用いられているアルミニウム合金箔では、その電気抵抗による発熱でゲージダウンができないという問題が生じ、電気効率等の電池特性に影響を及ぼすようになってきている。また、ゲージダウンを図るためには強度向上も必要となり、リチウムイオン電池の高容量化を可能とするため、高強度で且つ導電性に優れたアルミニウム箔が望まれている。
In recent years, there has been a demand for higher density and higher energy of lithium-ion batteries, and aluminum alloy foils that have been used as positive electrode collectors in the past have had the problem of being unable to gauge down due to heat generated by their electrical resistance, It has come to influence battery characteristics, such as electrical efficiency. Further, in order to reduce the gauge, it is necessary to improve the strength, and an aluminum foil having high strength and excellent conductivity is desired in order to increase the capacity of the lithium ion battery.
本発明は、リチウムイオン電池の正極集電体用アルミニウム箔における上記従来の問題を解決するために、成分組成、強度および電気抵抗値と電池特性との関係について試験、検討を重ねた結果としてなされたものであり、その目的は、従来材よりも高い強度と低い電気抵抗を示すリチウムイオン電池電極集電体用アルミニウム合金箔およびその製造方法を提供することにある。
The present invention has been made as a result of repeated tests and studies on the relationship between the component composition, strength, electrical resistance and battery characteristics in order to solve the above-described conventional problems in the aluminum foil for a positive electrode current collector of a lithium ion battery. It is an object of the present invention to provide an aluminum alloy foil for a lithium ion battery electrode current collector that exhibits higher strength and lower electrical resistance than conventional materials, and a method for producing the same.
上記の目的を達成するための請求項１によるリチウムイオン電池電極集電体用アルミニウム合金箔は、Ｍｎ：０．４％（質量％、以下同じ）以上０．８％未満、Ｍｇ：０．３％以上０．８％以下、Ｓｉ：０．４％以下（０％を含まず、以下同じ）、Ｆｅ：０．８％以下、Ｔｉ：０．０５％以下を含有し、ＭｎとＭｇの含有量についてＭｎ％＋４×Ｍｇ％≦３．２％の関係を満足し、残部Ａｌおよび不可避的不純物からなる組成を有し、引張強さが３００ＭＰａ以上、室温での比抵抗値が３．７μΩｃｍ以下であることを特徴とする。
In order to achieve the above object, an aluminum alloy foil for a lithium ion battery electrode current collector according to claim 1 has Mn: 0.4% (mass%, the same applies hereinafter) to less than 0.8%, Mg: 0.3 %: 0.8% or less, Si: 0.4% or less (excluding 0%, the same shall apply hereinafter), Fe: 0.8% or less, Ti: 0.05% or less, Mn and Mg contained It satisfies the relationship of Mn% + 4 × Mg% ≦ 3.2% with respect to the amount, has a composition composed of the balance Al and inevitable impurities, has a tensile strength of 300 MPa or more, and a specific resistance value at room temperature of 3.7 μΩcm or less It is characterized by being.
請求項２によるリチウムイオン電池電極集電体用アルミニウム合金箔は、請求項１において、アルミニウム合金箔が、さらに、Ｃｕ：０．０２％以上０．３％以下を含有することを特徴とする。
The aluminum alloy foil for a lithium ion battery electrode current collector according to claim 2 is characterized in that in claim 1, the aluminum alloy foil further contains Cu: 0.02% to 0.3%.
請求項３によるリチウムイオン電池電極集電体用アルミニウム合金箔の製造方法は、請求項１または請求項２記載のアルミニウム合金箔を製造する方法であって、請求項１または請求項２記載の組成を有するアルミニウム合金の鋳塊を常法に従って均質化処理した後、熱間圧延および冷間圧延を施し、冷間圧延において再結晶を伴う中間熱処理を行った後の最終冷間圧延率が８５％以上であることを特徴とする。
A method for producing an aluminum alloy foil for a lithium ion battery electrode current collector according to claim 3 is a method for producing an aluminum alloy foil according to claim 1 or 2, wherein the composition according to claim 1 or 2 is used. An ingot of an aluminum alloy having an aluminum alloy is homogenized according to a conventional method, then subjected to hot rolling and cold rolling, and a final cold rolling reduction rate after performing an intermediate heat treatment with recrystallization in the cold rolling is 85%. It is the above.
本発明によれば、特に正極材用として好適なリチウムイオン電池電極集電体用アルミニウム合金箔が提供される。当該アルミニウム合金箔は、正極板製造時の乾燥工程で加熱されても強度低下を生じることがなく、また圧延工程でも変形しない十分な強度を備えると共に、電気抵抗も十分に低く、リチウムイオン電池の高密度高エネルギー化が可能となる。
According to the present invention, there is provided an aluminum alloy foil for a lithium ion battery electrode current collector that is particularly suitable for a positive electrode material. The aluminum alloy foil does not cause a decrease in strength even when heated in the drying process at the time of manufacturing the positive electrode plate, and has sufficient strength not to be deformed even in the rolling process, and also has a sufficiently low electrical resistance. High density and high energy can be achieved.
本発明のアルミニウム合金箔における合金成分の意義およびその限定理由について説明する。
Ｍｎ：
固溶したＭｎは箔の強度を向上させるよう機能する。また、正極板製造時の乾燥工程での強度低下を抑制するが、固溶したＭｎは比抵抗を上昇させるので、導電性の観点からは含有量が少ないことが望ましい。Ｍｎの好ましい含有量は０．４％以上０．８％未満の範囲であり、０．４％未満では十分な強度を得ることができず、０．８％以上含有すると、室温での比抵抗値が３．７μΩｃｍを超えてしまうため好ましくない。Ｍｎのより好ましい含有範囲は０．５％以上０．７％以下である。 The significance of the alloy components in the aluminum alloy foil of the present invention and the reason for the limitation will be described.
Mn:
The dissolved Mn functions to improve the strength of the foil. Moreover, although the strength fall in the drying process at the time of positive electrode plate manufacture is suppressed, since solid solution Mn raises a specific resistance, it is desirable that there is little content from an electroconductive viewpoint. The preferable content of Mn is in the range of 0.4% or more and less than 0.8%. If the content is less than 0.4%, sufficient strength cannot be obtained. Since the value exceeds 3.7 μΩcm, it is not preferable. A more preferable content range of Mn is 0.5% or more and 0.7% or less.
Ｍｎ：
固溶したＭｎは箔の強度を向上させるよう機能する。また、正極板製造時の乾燥工程での強度低下を抑制するが、固溶したＭｎは比抵抗を上昇させるので、導電性の観点からは含有量が少ないことが望ましい。Ｍｎの好ましい含有量は０．４％以上０．８％未満の範囲であり、０．４％未満では十分な強度を得ることができず、０．８％以上含有すると、室温での比抵抗値が３．７μΩｃｍを超えてしまうため好ましくない。Ｍｎのより好ましい含有範囲は０．５％以上０．７％以下である。 The significance of the alloy components in the aluminum alloy foil of the present invention and the reason for the limitation will be described.
Mn:
The dissolved Mn functions to improve the strength of the foil. Moreover, although the strength fall in the drying process at the time of positive electrode plate manufacture is suppressed, since solid solution Mn raises a specific resistance, it is desirable that there is little content from an electroconductive viewpoint. The preferable content of Mn is in the range of 0.4% or more and less than 0.8%. If the content is less than 0.4%, sufficient strength cannot be obtained. Since the value exceeds 3.7 μΩcm, it is not preferable. A more preferable content range of Mn is 0.5% or more and 0.7% or less.
Ｍｇ：
ＭｇはＭｎと共に強度を向上させるよう機能し、また、Ｍｇの添加により比抵抗が上昇する。Ｍｇの好ましい含有量は０．３％以上０．８％以下の範囲であり、０．３％未満では強度が不足する。Ｍｇのより好ましい含有範囲は０．４％以上０．７％以下である。 Mg:
Mg functions to improve the strength together with Mn, and the specific resistance increases with the addition of Mg. The preferable content of Mg is in the range of 0.3% to 0.8%, and if it is less than 0.3%, the strength is insufficient. A more preferable content range of Mg is 0.4% or more and 0.7% or less.
ＭｇはＭｎと共に強度を向上させるよう機能し、また、Ｍｇの添加により比抵抗が上昇する。Ｍｇの好ましい含有量は０．３％以上０．８％以下の範囲であり、０．３％未満では強度が不足する。Ｍｇのより好ましい含有範囲は０．４％以上０．７％以下である。 Mg:
Mg functions to improve the strength together with Mn, and the specific resistance increases with the addition of Mg. The preferable content of Mg is in the range of 0.3% to 0.8%, and if it is less than 0.3%, the strength is insufficient. A more preferable content range of Mg is 0.4% or more and 0.7% or less.
リチウムイオン電池電極集電体の導電性を考慮すると、アルミニウム合金箔の比抵抗を３．７μΩｃｍ以下とすることが必要である。Ｍｇの比抵抗への影響はＭｎほど顕著ではないが、上記の観点から、Ｍｇ含有量とＭｎ含有量との関係は下記の式を満足しなければならない。
Ｍｎ％＋４×Ｍｇ％≦３．２％ Considering the conductivity of the lithium ion battery electrode current collector, the specific resistance of the aluminum alloy foil is required to be 3.7 μΩcm or less. Although the influence of Mg on the specific resistance is not as remarkable as Mn, from the above viewpoint, the relationship between the Mg content and the Mn content must satisfy the following formula.
Mn% + 4 × Mg% ≦ 3.2%
Ｍｎ％＋４×Ｍｇ％≦３．２％ Considering the conductivity of the lithium ion battery electrode current collector, the specific resistance of the aluminum alloy foil is required to be 3.7 μΩcm or less. Although the influence of Mg on the specific resistance is not as remarkable as Mn, from the above viewpoint, the relationship between the Mg content and the Mn content must satisfy the following formula.
Mn% + 4 × Mg% ≦ 3.2%
Ｓｉ：
Ｓｉは均質化処理や熱間圧延時にＡｌ－Ｍｎ－Ｓｉ系化合物を形成し、Ｍｎの固溶量を低下させる。Ｍｎ固溶量の低下が大きいと、冷間圧延時の加工硬化が抑制され、目標とする強度が得られなくなる。Ｓｉの好ましい含有量は０．４％以下の範囲である。Ｓｉ量をさらに低く抑えるには高純地金を使う必要があり、コストアップとなる。コスト、性能の両面を考慮したＳｉのより好ましい含有範囲は０．１５％以上０．３５％以下である。 Si:
Si forms an Al—Mn—Si based compound during homogenization treatment or hot rolling, and reduces the solid solution amount of Mn. When the decrease in the Mn solid solution amount is large, work hardening during cold rolling is suppressed, and the target strength cannot be obtained. A preferable content of Si is 0.4% or less. In order to keep the amount of Si even lower, it is necessary to use high purity bullion, which increases costs. A more preferable content range of Si considering both cost and performance is 0.15% or more and 0.35% or less.
Ｓｉは均質化処理や熱間圧延時にＡｌ－Ｍｎ－Ｓｉ系化合物を形成し、Ｍｎの固溶量を低下させる。Ｍｎ固溶量の低下が大きいと、冷間圧延時の加工硬化が抑制され、目標とする強度が得られなくなる。Ｓｉの好ましい含有量は０．４％以下の範囲である。Ｓｉ量をさらに低く抑えるには高純地金を使う必要があり、コストアップとなる。コスト、性能の両面を考慮したＳｉのより好ましい含有範囲は０．１５％以上０．３５％以下である。 Si:
Si forms an Al—Mn—Si based compound during homogenization treatment or hot rolling, and reduces the solid solution amount of Mn. When the decrease in the Mn solid solution amount is large, work hardening during cold rolling is suppressed, and the target strength cannot be obtained. A preferable content of Si is 0.4% or less. In order to keep the amount of Si even lower, it is necessary to use high purity bullion, which increases costs. A more preferable content range of Si considering both cost and performance is 0.15% or more and 0.35% or less.
Ｆｅ：
Ｆｅは鋳造時にＡｌ－Ｍｎ－Ｆｅ系化合物を形成し、Ｍｎの固溶量を低減させる。Ａｌ－Ｍｎ－Ｆｅ系化合物は１～１０μｍ程度のサイズで、強度には寄与しない。Ｆｅの含有量が０．８％を超えるとＭｎの固溶量が減少し、所定の強度が得られなくなる。また、鋳造時に粗大なＡｌ－Ｍｎ－Ｆｅ系晶出物が形成し易くなり、箔圧延時にピンホール発生の原因となる。粗大晶出物形成を防ぐためには、Ｍｇの添加を考慮して、（Ｆｅ％＋Ｍｎ％）が１．４％以下となるよう配合量を調整することが必要である。Ｆｅ量を低く抑えるには高純地金を使う必要があり、コストアップとなるから、コスト、性能の両面を考慮したＦｅのより好ましい含有範囲は０．４％以上０．７％以下である。 Fe:
Fe forms an Al—Mn—Fe-based compound at the time of casting, and reduces the solid solution amount of Mn. Al—Mn—Fe based compounds have a size of about 1 to 10 μm and do not contribute to strength. If the Fe content exceeds 0.8%, the solid solution amount of Mn decreases, and a predetermined strength cannot be obtained. In addition, coarse Al—Mn—Fe-based crystals are easily formed during casting, causing pinholes during foil rolling. In order to prevent the formation of coarse crystals, it is necessary to adjust the blending amount so that (Fe% + Mn%) is 1.4% or less in consideration of the addition of Mg. In order to keep the amount of Fe low, it is necessary to use high-purity bullion, which increases costs. Therefore, a more preferable range of Fe in consideration of both cost and performance is 0.4% or more and 0.7% or less. .
Ｆｅは鋳造時にＡｌ－Ｍｎ－Ｆｅ系化合物を形成し、Ｍｎの固溶量を低減させる。Ａｌ－Ｍｎ－Ｆｅ系化合物は１～１０μｍ程度のサイズで、強度には寄与しない。Ｆｅの含有量が０．８％を超えるとＭｎの固溶量が減少し、所定の強度が得られなくなる。また、鋳造時に粗大なＡｌ－Ｍｎ－Ｆｅ系晶出物が形成し易くなり、箔圧延時にピンホール発生の原因となる。粗大晶出物形成を防ぐためには、Ｍｇの添加を考慮して、（Ｆｅ％＋Ｍｎ％）が１．４％以下となるよう配合量を調整することが必要である。Ｆｅ量を低く抑えるには高純地金を使う必要があり、コストアップとなるから、コスト、性能の両面を考慮したＦｅのより好ましい含有範囲は０．４％以上０．７％以下である。 Fe:
Fe forms an Al—Mn—Fe-based compound at the time of casting, and reduces the solid solution amount of Mn. Al—Mn—Fe based compounds have a size of about 1 to 10 μm and do not contribute to strength. If the Fe content exceeds 0.8%, the solid solution amount of Mn decreases, and a predetermined strength cannot be obtained. In addition, coarse Al—Mn—Fe-based crystals are easily formed during casting, causing pinholes during foil rolling. In order to prevent the formation of coarse crystals, it is necessary to adjust the blending amount so that (Fe% + Mn%) is 1.4% or less in consideration of the addition of Mg. In order to keep the amount of Fe low, it is necessary to use high-purity bullion, which increases costs. Therefore, a more preferable range of Fe in consideration of both cost and performance is 0.4% or more and 0.7% or less. .
Ｔｉ：
Ｔｉは鋳塊組織の微細化のために添加される。Ｔｉは少量でも比抵抗を上昇させるが、０．０５％を超えて含有すると箔圧延時のピンホール発生の原因となることがある。ＢはＴｉと共に添加することにより同様な効果を得ることができる。アルミニウム合金箔中のＢの含有量は同様の理由で０．０１％以下とするのが好ましい。 Ti:
Ti is added to refine the ingot structure. Ti increases the specific resistance even in a small amount, but if it exceeds 0.05%, it may cause pinholes during foil rolling. The same effect can be obtained by adding B together with Ti. For the same reason, the content of B in the aluminum alloy foil is preferably 0.01% or less.
Ｔｉは鋳塊組織の微細化のために添加される。Ｔｉは少量でも比抵抗を上昇させるが、０．０５％を超えて含有すると箔圧延時のピンホール発生の原因となることがある。ＢはＴｉと共に添加することにより同様な効果を得ることができる。アルミニウム合金箔中のＢの含有量は同様の理由で０．０１％以下とするのが好ましい。 Ti:
Ti is added to refine the ingot structure. Ti increases the specific resistance even in a small amount, but if it exceeds 0.05%, it may cause pinholes during foil rolling. The same effect can be obtained by adding B together with Ti. For the same reason, the content of B in the aluminum alloy foil is preferably 0.01% or less.
Ｃｕ：
Ｃｕは強度を向上させるよう機能する。Ｃｕの好ましい含有量は０．０２％以上０．３％以下の範囲であり、０．０２％未満では強度向上効果が十分でない。ＣｕはＭｎよりも比抵抗増加への影響は少ないが、０．３％を超えて含有すると、強度は上昇するが比抵抗も増加して好ましくない。また、鋳造時に割れが発生し易くなり、量産規模の製造が難しくなる。Ｃｕのより好ましい含有範囲は０．０３％以上０．１５％以下である。 Cu:
Cu functions to improve strength. The preferable content of Cu is in the range of 0.02% to 0.3%, and if it is less than 0.02%, the strength improvement effect is not sufficient. Cu has less influence on the increase in specific resistance than Mn, but if it exceeds 0.3%, the strength increases but the specific resistance also increases, which is not preferable. In addition, cracks are likely to occur during casting, making it difficult to manufacture on a mass production scale. A more preferable content range of Cu is 0.03% or more and 0.15% or less.
Ｃｕは強度を向上させるよう機能する。Ｃｕの好ましい含有量は０．０２％以上０．３％以下の範囲であり、０．０２％未満では強度向上効果が十分でない。ＣｕはＭｎよりも比抵抗増加への影響は少ないが、０．３％を超えて含有すると、強度は上昇するが比抵抗も増加して好ましくない。また、鋳造時に割れが発生し易くなり、量産規模の製造が難しくなる。Ｃｕのより好ましい含有範囲は０．０３％以上０．１５％以下である。 Cu:
Cu functions to improve strength. The preferable content of Cu is in the range of 0.02% to 0.3%, and if it is less than 0.02%, the strength improvement effect is not sufficient. Cu has less influence on the increase in specific resistance than Mn, but if it exceeds 0.3%, the strength increases but the specific resistance also increases, which is not preferable. In addition, cracks are likely to occur during casting, making it difficult to manufacture on a mass production scale. A more preferable content range of Cu is 0.03% or more and 0.15% or less.
不可避的不純物としては、Ｚｎ：０．１％以下、Ｃｒ、Ｎｉ、Ｇａ、Ｖ、その他の元素は個々に０．０５％以下、合計で０．１５％以下であれば本発明の特性に影響することはない。
As unavoidable impurities, Zn: 0.1% or less, Cr, Ni, Ga, V, and other elements individually 0.05% or less, if the total is 0.15% or less, the characteristics of the present invention are affected. Never do.
本発明のリチウムイオン電池電極集電体用アルミニウム合金箔においては、圧延工程で変形を生じないために、引張強さが３００ＭＰａ以上の十分な強度を有することが必要である。
In the aluminum alloy foil for a lithium ion battery electrode current collector of the present invention, it is necessary that the tensile strength has a sufficient strength of 300 MPa or more in order to prevent deformation in the rolling process.
本発明のアルミニウム合金箔の製造工程について説明する。
前記の組成を有するアルミニウム合金を溶解、鋳造して、所定のスラブに造塊し、得られたスラブ（鋳塊）を常法に従って均質化処理した後、熱間圧延を行う。リチウムイオン電池電極集電体用としては厚さ２０μｍ以下の箔材に仕上げる必要があり、熱間圧延板から中間熱処理を行うことなく、このような薄箔まで冷間圧延することは加工硬化による強度上昇のため量産上困難である。従って、圧延途中で再結晶を伴う中間熱処理を施して冷間圧延を行う。この場合、所定の強度を得るためには、冷間圧延において再結晶を伴う中間熱処理を行った後の最終冷間圧延率を８５％以上とすることが必要である。 The manufacturing process of the aluminum alloy foil of the present invention will be described.
The aluminum alloy having the above composition is melted and cast to form a predetermined slab, and the obtained slab (ingot) is homogenized according to a conventional method, followed by hot rolling. For a lithium ion battery electrode current collector, it is necessary to finish the foil material with a thickness of 20 μm or less, and cold rolling to such a thin foil without performing an intermediate heat treatment from a hot rolled plate is due to work hardening. Difficult for mass production due to increased strength. Therefore, cold rolling is performed by performing an intermediate heat treatment accompanied by recrystallization during rolling. In this case, in order to obtain a predetermined strength, it is necessary to set the final cold rolling rate after performing the intermediate heat treatment accompanied by recrystallization in cold rolling to 85% or more.
前記の組成を有するアルミニウム合金を溶解、鋳造して、所定のスラブに造塊し、得られたスラブ（鋳塊）を常法に従って均質化処理した後、熱間圧延を行う。リチウムイオン電池電極集電体用としては厚さ２０μｍ以下の箔材に仕上げる必要があり、熱間圧延板から中間熱処理を行うことなく、このような薄箔まで冷間圧延することは加工硬化による強度上昇のため量産上困難である。従って、圧延途中で再結晶を伴う中間熱処理を施して冷間圧延を行う。この場合、所定の強度を得るためには、冷間圧延において再結晶を伴う中間熱処理を行った後の最終冷間圧延率を８５％以上とすることが必要である。 The manufacturing process of the aluminum alloy foil of the present invention will be described.
The aluminum alloy having the above composition is melted and cast to form a predetermined slab, and the obtained slab (ingot) is homogenized according to a conventional method, followed by hot rolling. For a lithium ion battery electrode current collector, it is necessary to finish the foil material with a thickness of 20 μm or less, and cold rolling to such a thin foil without performing an intermediate heat treatment from a hot rolled plate is due to work hardening. Difficult for mass production due to increased strength. Therefore, cold rolling is performed by performing an intermediate heat treatment accompanied by recrystallization during rolling. In this case, in order to obtain a predetermined strength, it is necessary to set the final cold rolling rate after performing the intermediate heat treatment accompanied by recrystallization in cold rolling to 85% or more.
以下、本発明の実施例を比較例と対比して説明し、その効果を実証する。なお、これらの実施例は本発明の一実施態様を示すものであり、本発明はこれらに限定されない。
Hereinafter, examples of the present invention will be described in comparison with comparative examples, and their effects will be verified. In addition, these Examples show one embodiment of this invention, and this invention is not limited to these.
実施例１
表１に示す組成を有するアルミニウム合金（Ａ～Ｋ）を溶解、半連続鋳造法により造塊し、得られた鋳塊を４８０℃の温度で５ｈ均質化処理した後、４５０～２６０℃の温度範囲で熱間圧延を行い、厚さ３ｍｍの熱間圧延板を得た。熱間圧延板を厚さ０．５ｍｍまで冷間圧延した後、急速加熱炉を用いて４００℃の温度で１分間保持し、２０℃／ｓの冷却速度で冷却する中間熱処理を実施し、中間熱処理以後は、冷間圧延を繰り返して１５μｍのアルミニウム合金箔（試験材１～１１）を得た。この時の冷間圧延率は９７％であった。なお、従来材（試験材１１）（合金：３００３合金）については、均質化処理を６００℃の温度で５ｈ行った以外は、同じ工程で箔材を作成した。 Example 1
Aluminum alloys (A to K) having the composition shown in Table 1 were melted and ingot-formed by a semi-continuous casting method, and the resulting ingot was homogenized at a temperature of 480 ° C. for 5 hours, and then a temperature of 450 to 260 ° C. Hot rolling was performed in the range to obtain a hot rolled plate having a thickness of 3 mm. After cold-rolling the hot-rolled sheet to a thickness of 0.5 mm, an intermediate heat treatment is performed using a rapid heating furnace at a temperature of 400 ° C. for 1 minute and cooling at a cooling rate of 20 ° C./s After the heat treatment, cold rolling was repeated to obtain 15 μm aluminum alloy foils (test materials 1 to 11). The cold rolling rate at this time was 97%. In addition, about the conventional material (test material 11) (alloy: 3003 alloy), the foil material was created in the same process except performing the homogenization process for 5 hours at the temperature of 600 degreeC.
表１に示す組成を有するアルミニウム合金（Ａ～Ｋ）を溶解、半連続鋳造法により造塊し、得られた鋳塊を４８０℃の温度で５ｈ均質化処理した後、４５０～２６０℃の温度範囲で熱間圧延を行い、厚さ３ｍｍの熱間圧延板を得た。熱間圧延板を厚さ０．５ｍｍまで冷間圧延した後、急速加熱炉を用いて４００℃の温度で１分間保持し、２０℃／ｓの冷却速度で冷却する中間熱処理を実施し、中間熱処理以後は、冷間圧延を繰り返して１５μｍのアルミニウム合金箔（試験材１～１１）を得た。この時の冷間圧延率は９７％であった。なお、従来材（試験材１１）（合金：３００３合金）については、均質化処理を６００℃の温度で５ｈ行った以外は、同じ工程で箔材を作成した。 Example 1
Aluminum alloys (A to K) having the composition shown in Table 1 were melted and ingot-formed by a semi-continuous casting method, and the resulting ingot was homogenized at a temperature of 480 ° C. for 5 hours, and then a temperature of 450 to 260 ° C. Hot rolling was performed in the range to obtain a hot rolled plate having a thickness of 3 mm. After cold-rolling the hot-rolled sheet to a thickness of 0.5 mm, an intermediate heat treatment is performed using a rapid heating furnace at a temperature of 400 ° C. for 1 minute and cooling at a cooling rate of 20 ° C./s After the heat treatment, cold rolling was repeated to obtain 15 μm aluminum alloy foils (test materials 1 to 11). The cold rolling rate at this time was 97%. In addition, about the conventional material (test material 11) (alloy: 3003 alloy), the foil material was created in the same process except performing the homogenization process for 5 hours at the temperature of 600 degreeC.
試験材（アルミニウム合金箔）について、引張特性および室温（２５℃）の比抵抗値を測定した。結果を表２に示す。
The tensile properties and the specific resistance value at room temperature (25 ° C.) were measured for the test material (aluminum alloy foil). The results are shown in Table 2.
表２に示すように、本発明に従う試験材１～５は、引張強さが３００ＭＰａ以上で、室温での比抵抗は３．７μΩｃｍ以下となり、従来材（試験材１１）の３００３合金箔よりも強度が高く、比抵抗が低減されている。
As shown in Table 2, the test materials 1 to 5 according to the present invention have a tensile strength of 300 MPa or more and a specific resistance at room temperature of 3.7 μΩcm or less, which is higher than that of the conventional material (test material 11) 3003 alloy foil. The strength is high and the specific resistance is reduced.
これに対して本発明の条件を外れた試験材６～１０は、引張強さ、比抵抗のいずれかにおいて劣っていた。すなわち、試験材６はＭｎ量が多いため比抵抗が高くなった。試験材７は、（Ｍｎ％＋４×Ｍｇ％）が３．２％より大きいため比抵抗値が高くなった。
On the other hand, the test materials 6 to 10 outside the conditions of the present invention were inferior in either tensile strength or specific resistance. That is, since the test material 6 had a large amount of Mn, the specific resistance was high. Since the test material 7 had (Mn% + 4 × Mg%) larger than 3.2%, the specific resistance value was high.
試験材８はＭｎ量が少ないため引張強さが３００ＭＰａ未満となった。試験材９はＦｅ量が多く、鋳造時にＡｌ－Ｍｎ－Ｆｅ系化合物が生成してＭｎの固溶量が減少したため、引張強さが３００ＭＰａ未満となった。試験材１０はＳｉ量が多くＭｎ固溶量が減少したため、また、Ｍｇ量が少ないため、引張強さが３００ＭＰａ未満となった。試験材１１は従来材の３００３合金箔の特性を示し、引張強さは３００ＭＰａ未満であり、比抵抗は３．７μΩｃｍを超えている。
Since the test material 8 had a small amount of Mn, the tensile strength was less than 300 MPa. The test material 9 had a large amount of Fe, and an Al—Mn—Fe-based compound was produced during casting to reduce the solid solution amount of Mn. Therefore, the tensile strength was less than 300 MPa. Since the test material 10 had a large amount of Si and a decreased amount of Mn solid solution, and the amount of Mg was small, the tensile strength was less than 300 MPa. The test material 11 shows the characteristics of a conventional 3003 alloy foil, the tensile strength is less than 300 MPa, and the specific resistance exceeds 3.7 μΩcm.
実施例２
実施例１で造塊した合金Ｅを用い、実施例１における試験材１～１０の製造と同じ条件で、均質化処置、熱間圧延、冷間圧延を行い、最終冷間圧延率のみを変えて厚さ１５μｍのアルミニウム合金箔を製造し、得られた合金箔（試験材）について、実施例１と同様に引張特性と室温（２５℃）の比抵抗を測定した。結果を表３に示す。 Example 2
Using alloy E ingoted in Example 1, homogenization treatment, hot rolling and cold rolling were performed under the same conditions as in the production of test materials 1 to 10 in Example 1, and only the final cold rolling rate was changed. An aluminum alloy foil having a thickness of 15 μm was manufactured, and the obtained alloy foil (test material) was measured for tensile properties and specific resistance at room temperature (25 ° C.) in the same manner as in Example 1. The results are shown in Table 3.
実施例１で造塊した合金Ｅを用い、実施例１における試験材１～１０の製造と同じ条件で、均質化処置、熱間圧延、冷間圧延を行い、最終冷間圧延率のみを変えて厚さ１５μｍのアルミニウム合金箔を製造し、得られた合金箔（試験材）について、実施例１と同様に引張特性と室温（２５℃）の比抵抗を測定した。結果を表３に示す。 Example 2
Using alloy E ingoted in Example 1, homogenization treatment, hot rolling and cold rolling were performed under the same conditions as in the production of test materials 1 to 10 in Example 1, and only the final cold rolling rate was changed. An aluminum alloy foil having a thickness of 15 μm was manufactured, and the obtained alloy foil (test material) was measured for tensile properties and specific resistance at room temperature (25 ° C.) in the same manner as in Example 1. The results are shown in Table 3.
表３に示すように、本発明に従う試験材１２～１４は、引張強さ３００ＭＰａ以上、室温での比抵抗３．７μΩｃｍ以下の特性を示した。
As shown in Table 3, the test materials 12 to 14 according to the present invention exhibited characteristics of a tensile strength of 300 MPa or more and a specific resistance at room temperature of 3.7 μΩcm or less.
これに対して、試験材１５～１７はいずれも、最終冷間圧延率が８５％より少ないため、引張強さが３００ＭＰａより低いものとなった。
On the other hand, all of the test materials 15 to 17 had a tensile strength lower than 300 MPa because the final cold rolling rate was less than 85%.
Claims (3)
- Ｍｎ：０．４％（質量％、以下同じ）以上０．８％未満、Ｍｇ：０．３％以上０．８％以下、Ｓｉ：０．４％以下（０％を含まず、以下同じ）、Ｆｅ：０．８％以下、Ｔｉ：０．０５％以下を含有し、ＭｎとＭｇの含有量についてＭｎ％＋４×Ｍｇ％≦３．２％の関係を満足し、残部Ａｌおよび不可避的不純物からなる組成を有し、引張強さが３００ＭＰａ以上、室温での比抵抗値が３．７μΩｃｍ以下であることを特徴とするリチウムイオン電池電極集電体用アルミニウム合金箔。 Mn: 0.4% (mass%, the same shall apply hereinafter) or more and less than 0.8%, Mg: 0.3% or more and 0.8% or less, Si: 0.4% or less (excluding 0%, the same shall apply hereinafter) Fe: 0.8% or less, Ti: 0.05% or less, satisfying the relationship of Mn% + 4 × Mg% ≦ 3.2% with respect to the contents of Mn and Mg, the balance Al and inevitable impurities An aluminum alloy foil for a lithium ion battery electrode current collector, characterized in that it has a tensile strength of 300 MPa or more and a specific resistance value at room temperature of 3.7 μΩcm or less.
- 前記アルミニウム合金箔が、さらに、Ｃｕ：０．０２％以上０．３％以下を含有することを特徴とする請求項１記載のリチウムイオン電池電極集電体用アルミニウム合金箔。 The aluminum alloy foil for a lithium ion battery electrode current collector according to claim 1, wherein the aluminum alloy foil further contains Cu: 0.02% or more and 0.3% or less.
- 請求項１または請求項２記載のアルミニウム合金箔を製造する方法であって、請求項１または請求項２記載の組成を有するアルミニウム合金の鋳塊を常法に従って均質化処理した後、熱間圧延および冷間圧延を施し、冷間圧延において再結晶を伴う中間熱処理を行った後の最終冷間圧延率が８５％以上であることを特徴とするリチウムイオン電池電極集電体用アルミニウム合金箔の製造方法。 A method for producing an aluminum alloy foil according to claim 1 or 2, wherein the ingot of the aluminum alloy having the composition according to claim 1 or 2 is homogenized according to a conventional method, and then hot rolled. An aluminum alloy foil for a lithium ion battery electrode current collector, wherein the final cold rolling rate after performing cold rolling and performing intermediate heat treatment accompanied by recrystallization in cold rolling is 85% or more Production method.
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| JP2011041154A JP2012177171A (en) | 2011-02-28 | 2011-02-28 | Aluminum alloy foil for lithium ion battery electrode current collector, and method for producing the same |
| JP2011-041154 | 2011-02-28 |
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| CN110943226A (en) * | 2019-04-28 | 2020-03-31 | 宁德时代新能源科技股份有限公司 | Positive current collector, positive pole piece and electrochemical device |
| CN112941374A (en) * | 2021-02-26 | 2021-06-11 | 永杰新材料股份有限公司 | Battery aluminum foil and processing method thereof |
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| JP5945148B2 (en) * | 2012-04-13 | 2016-07-05 | 三菱アルミニウム株式会社 | Aluminum alloy foil for lithium ion secondary battery positive electrode current collector and lithium ion secondary battery using the same |
| JP6435588B2 (en) * | 2013-07-08 | 2018-12-12 | 三菱アルミニウム株式会社 | Aluminum alloy foil for positive electrode current collector of lithium ion secondary battery |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2004332106A (en) * | 2003-04-15 | 2004-11-25 | Nippon Light Metal Co Ltd | Aluminum alloy sheet with excellent press formability and continuous resistance spot weldability, and its manufacturing method |
| JP2008150651A (en) * | 2006-12-15 | 2008-07-03 | Mitsubishi Alum Co Ltd | Aluminum alloy foil with excellent bending resistance for lithium-ion battery electrode material, and its manufacturing method |
| JP2009064560A (en) * | 2006-08-29 | 2009-03-26 | Toyo Aluminium Kk | Aluminum alloy foil for current collector |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2004332106A (en) * | 2003-04-15 | 2004-11-25 | Nippon Light Metal Co Ltd | Aluminum alloy sheet with excellent press formability and continuous resistance spot weldability, and its manufacturing method |
| JP2009064560A (en) * | 2006-08-29 | 2009-03-26 | Toyo Aluminium Kk | Aluminum alloy foil for current collector |
| JP2008150651A (en) * | 2006-12-15 | 2008-07-03 | Mitsubishi Alum Co Ltd | Aluminum alloy foil with excellent bending resistance for lithium-ion battery electrode material, and its manufacturing method |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110943226A (en) * | 2019-04-28 | 2020-03-31 | 宁德时代新能源科技股份有限公司 | Positive current collector, positive pole piece and electrochemical device |
| CN112941374A (en) * | 2021-02-26 | 2021-06-11 | 永杰新材料股份有限公司 | Battery aluminum foil and processing method thereof |
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