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WO2013008314A1 - Matériau de tôle d'alliage d'aluminium pour des boîtiers de batterie au lithium-ion - Google Patents

Matériau de tôle d'alliage d'aluminium pour des boîtiers de batterie au lithium-ion Download PDF

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Publication number
WO2013008314A1
WO2013008314A1 PCT/JP2011/065877 JP2011065877W WO2013008314A1 WO 2013008314 A1 WO2013008314 A1 WO 2013008314A1 JP 2011065877 W JP2011065877 W JP 2011065877W WO 2013008314 A1 WO2013008314 A1 WO 2013008314A1
Authority
WO
WIPO (PCT)
Prior art keywords
aluminum alloy
lithium ion
ion battery
mpa
alloy plate
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.)
Ceased
Application number
PCT/JP2011/065877
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English (en)
Japanese (ja)
Inventor
浩一郎 滝口
田中　宏樹
福田　敏彦
日比野　淳
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Sumitomo Light Metal Industries Ltd
Original Assignee
Sumitomo Light Metal Industries Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Sumitomo Light Metal Industries Ltd filed Critical Sumitomo Light Metal Industries Ltd
Priority to PCT/JP2011/065877 priority Critical patent/WO2013008314A1/fr
Priority to CN201180072252.XA priority patent/CN103748245B/zh
Publication of WO2013008314A1 publication Critical patent/WO2013008314A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M50/00—Constructional details or processes of manufacture of the non-active parts of electrochemical cells other than fuel cells, e.g. hybrid cells
    • H01M50/10—Primary casings; Jackets or wrappings
    • H01M50/116—Primary casings; Jackets or wrappings characterised by the material
    • H01M50/117—Inorganic material
    • H01M50/119—Metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M50/00—Constructional details or processes of manufacture of the non-active parts of electrochemical cells other than fuel cells, e.g. hybrid cells
    • H01M50/10—Primary casings; Jackets or wrappings
    • H01M50/131—Primary casings; Jackets or wrappings characterised by physical properties, e.g. gas permeability, size or heat resistance
    • H01M50/133—Thickness
    • 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
    • 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 relates to an aluminum alloy plate material for a lithium ion battery case, which is suitable as a case material for a lithium ion battery used in automobiles, mobile phones, digital cameras, etc., has excellent laser weldability and can reduce the explosion-proof valve operating pressure.
  • Lithium-ion battery case is made by combining a can material formed by deep-drawing an aluminum plate or an iron plate with a sealing material formed by press-molding an aluminum plate, enclosing an internal structure such as an electrode, and then the can material and the sealing material. It is produced by laser welding around the joint.
  • the sealing material is required to have high strength after press processing, a large penetration depth during laser welding, and to obtain a high bonding strength.
  • an explosion-proof valve (a part having a locally reduced plate thickness) is arranged for the purpose of releasing the internal pressure before the battery bursts.
  • this explosion-proof valve There are two methods for forming this explosion-proof valve: one is to integrally form the sealing material by press processing, and the other is to paste the foil material to the sealed sealing material by laser welding. Therefore, the former forming method is preferred.
  • A1050 and A3003 have been mainly used so far.
  • A1050 is excellent in workability, it has the disadvantages of low strength after processing and inferior in laser weldability.
  • A3003 is high in strength after processing and excellent in laser weldability. Since the valve portion is work-hardened, heat treatment is required to adjust the operating pressure of the explosion-proof valve, which is a big problem in terms of cost.
  • Al-Mn-Si-Fe alloys with improved crack propagation in the explosion-proof valve part as an aluminum material for sealing materials, and improved laser weldability and reduced work hardenability (press Al—Fe—Mn alloys and the like aimed at reducing the heat treatment process after processing have been proposed.
  • the proposed one has improved crack propagation compared to A3003, reduced work hardenability, and does not require heat treatment after press working, but the hardness of the explosion-proof valve increases due to work hardening. Because of the problem that the operating pressure of the explosion-proof valve becomes higher than the design pressure, the required characteristics cannot be satisfied.
  • JP 2006-037129 A Japanese Patent No. 4281727
  • the inventor has developed a fine intermetallic compound that is inconsistent with the parent phase when the accumulated amount of dislocations is increased by cold working in the study process for obtaining an aluminum material that can solve the above-mentioned conventional problems in the sealing material. It has been found that dislocation disappears, and it is possible to develop a state where it is hardened and softened only in the explosion-proof valve processing region except in the explosion-proof valve processing region.
  • the present invention has been made as a result of repeated tests and examinations based on the above knowledge, and its purpose is for a lithium ion battery case that can reduce the explosion-proof valve operating pressure and is excellent in laser weldability.
  • the object is to provide an aluminum alloy sheet.
  • the aluminum alloy sheet for a lithium ion battery case according to claim 1 for achieving the above object comprises Fe: 0.5 to 2.0% and Si: 0.03 to 0.3% by mass.
  • An aluminum alloy sheet for a lithium ion battery case according to claim 2 is the aluminum alloy sheet according to claim 1, wherein the aluminum alloy sheet further includes Ti: 0.20% or less, Zr: 0.20% or less, Cr: 0.30% or less. 1 type or 2 types or more of them are contained.
  • the aluminum alloy sheet for a lithium ion battery case according to claim 3 is characterized in that, in claim 1 or 2, the aluminum alloy sheet further contains B: 5 to 100 ppm.
  • the work is hardened and hardened up to a cold work degree of about 70%, but the material is hard to work hard at a cold work degree of 90% or more in the explosion-proof valve working area.
  • An aluminum alloy plate material for a lithium ion battery case particularly an aluminum alloy plate material suitable as a sealing material for a lithium ion battery, which can achieve both high strength and low explosion-proof valve operating pressure is provided.
  • Fe is an important element that functions to generate a fine Al—Fe-based compound that is inconsistent with the matrix (matrix) and is difficult to work harden in a high workability range. It also has the effect of increasing the absorption rate of the YAG laser used for joining lithium ion batteries and increasing the penetration depth during laser welding.
  • the preferred content is in the range of 0.5 to 2.0%, and if it is less than 0.5%, it becomes difficult to work harden in the high workability range (hereinafter simply referred to as hard work hardenability). When the penetration depth at the time of laser welding is not sufficient and the content exceeds 2.0%, a coarse intermetallic compound is generated, and press workability is lowered.
  • a more preferable content range of Fe is 1.0 to 1.8%.
  • Si is easily dissolved in the manufacturing process, and if it exceeds 0.3%, it becomes difficult to express characteristics that are difficult to work harden.
  • Si is an element contained as an inevitable impurity in the aluminum ingot. If it is limited to less than 0.03%, it is not preferable because a high-purity aluminum ingot must be used, resulting in an increase in cost. Accordingly, the preferable content of Si is in the range of 0.03 to 0.3%, and the more preferable content range is 0.05 to 0.20%.
  • Cu, Mn, Mg, and Zn which are impurities that easily dissolve, are preferably limited to 0.10% or less in order to inhibit the expression of properties that are difficult to work harden. More preferably, it is limited to the following.
  • Ti, Zr, Cr, and B can be added for the purpose of preventing cracking during welding (structural refinement by nucleation during solidification).
  • Preferable contents are Ti: 0.20% or less, Zr: 0.20% or less, Cr: 0.30% or less, and B: 5 to 100 ppm, respectively. And press workability is reduced.
  • the size and number of distributions of the Al—Fe-based intermetallic compound are important factors for developing characteristics that make it difficult to work harden.
  • An intermetallic compound having an equivalent circle diameter of more than 30 nm is less likely to be a dislocation disappearance site, and has less influence on the development of properties that are difficult to work harden. If the distribution number of particles having an equivalent circle diameter of 5 to 30 nm is less than 1000 / mm 3 , dislocation disappearance sites are insufficient, and the development of characteristics that make it difficult to work harden becomes insufficient.
  • control of the size and distribution number of the Al—Fe intermetallic compound and reduction of the Si solid solution amount are important factors.
  • a known semi-continuous casting method can be applied for casting, but the ingot homogenization is an important process for promoting fine precipitation of Al—Fe intermetallic compounds.
  • the homogenization treatment is preferably performed in a temperature range of 450 to 540 ° C.
  • the temperature is lower than 450 ° C., precipitation of the Al—Fe-based intermetallic compound is not sufficient, and when it exceeds 540 ° C., the Al—Fe-based intermetallic compound is aggregated and coarsened, and Fe is re-dissolved.
  • the homogenization time is preferably 3 to 24 hours. If it is less than 3 hours, the precipitation of the Al—Fe-based intermetallic compound is not sufficient, and if it exceeds 24 hours, the production cost increases.
  • hot rolling is performed.
  • the hot rolling preferably starts at 400 to 450 ° C. and ends at 200 to 250 ° C.
  • the structure after hot rolling becomes a non-recrystallized structure.
  • intermediate annealing For the purpose of improving properties that are difficult to work harden, it is preferable to perform intermediate annealing immediately after hot rolling.
  • processing strain introduced by hot rolling is used as a precipitation site to promote fine precipitation of Al-Fe-based intermetallic compounds, and at the same time, Si precipitates that hinder the development of properties that are difficult to work harden. And the characteristic which becomes hard to work harden
  • the annealing temperature is preferably 260 to 400 ° C.
  • the heating rate up to the annealing temperature is preferably 20 to 100 ° C./h.
  • the heating rate is less than 20 ° C./h, the production cost increases, which is not preferable.
  • the heating rate exceeds 100 ° C./h, the precipitation of Si becomes insufficient, and the characteristics that are difficult to work harden cannot be obtained sufficiently.
  • a more preferable heating rate is 30 to 60 ° C./h.
  • the cooling rate has little influence on the development of characteristics that make it difficult to work harden, but it is essential to use a batch furnace because of the heating rate.
  • cold rolling is performed to obtain a predetermined plate thickness.
  • cold rolling since it has little influence with respect to the expression of the characteristic which becomes difficult to work harden
  • Final annealing (intermediate annealing in the case of H1n tempering) is performed after cold rolling.
  • Final annealing is an important process for obtaining characteristics that are difficult to work harden along with the homogenization treatment.
  • the final annealing increases the elongation by recrystallization, improves the press formability, and promotes the fine precipitation of the Al-Fe-based intermetallic compound using the processing strain introduced in the cold rolling as a precipitation site.
  • the object is to precipitate Si that hinders the expression of properties that are difficult to work harden, and to reduce the solid solution amount of Si.
  • the final annealing temperature is preferably 260 to 400 ° C.
  • the annealing temperature is less than 260 ° C., recrystallization is insufficient, press formability is deteriorated, and precipitation of Al—Fe intermetallic compound is insufficient.
  • the annealing temperature is less than 260 ° C.
  • recrystallization is insufficient
  • press formability is deteriorated
  • precipitation of Al—Fe intermetallic compound is insufficient.
  • 400 ° C. or higher since Si is dissolved, characteristics that are difficult to work harden cannot be obtained sufficiently.
  • the heating rate to the final annealing temperature is preferably 20 to 100 ° C./h. If the heating rate is less than 20 ° C./h, the production cost increases, which is not preferable. If the heating rate exceeds 100 ° C./h, the precipitation of Si becomes insufficient, and the characteristics that make it difficult to work harden cannot be obtained sufficiently.
  • the cooling rate has little influence on the development of characteristics that are difficult to work harden, but because of the heating rate, the use of a batch furnace is essential, and the furnace may be cooled in accordance with a conventional method.
  • the aluminum alloy sheet for lithium ion battery case of the present invention can be used as H1n tempering by cold rolling after final annealing in accordance with the required strength level. Even in the case of H1n refining, the properties that are difficult to work harden can be obtained without any problem, but since the press formability decreases as the elongation decreases, the final annealing treatment conditions are considered in consideration of the balance between strength and press formability. It is necessary to adjust the cold rolling rate after final annealing.
  • Example 1 Aluminum alloys (A to F) having the compositions shown in Table 1 were melted and formed into an ingot having a thickness of 500 mm by a semi-continuous casting method. After the obtained ingot was homogenized at 500 ° C. for 8 hours, the rolled surfaces were each 8 mm chamfered and removed, then hot rolling was started at 440 ° C., and hot rolling was terminated at 230 ° C., A hot rolled sheet having a thickness of 5.0 mm was obtained.
  • test materials 1 to 6 (tempered) : O material).
  • Example 2 An aluminum alloy (G) having the composition shown in Table 1 was melted and cast, homogenized, and hot-rolled in the same manner as in Example 1, and then subjected to intermediate annealing at 300 ° C. for 3 h (heating rate 50 ° C./h). Then, cold-rolled to a thickness of 0.8 mm (cold rolling rate of 84%), and further subjected to final annealing at 300 ° C. for 3 h (heating rate 50 ° C./h) to obtain test material 7 (tempering) : O material).
  • Example 3 The aluminum alloy (H) having the composition shown in Table 1 was melted and cast, homogenized, and hot-rolled in the same manner as in Example 1, and then cold-rolled to a thickness of 3.2 mm (cold rolling rate of 36%) Then, after intermediate annealing at 300 ° C. for 3 h (heating rate 50 ° C./h), cold rolling to a thickness of 0.8 mm (cold rolling rate of 75%) was performed, and test material 8 (tempering: H16 material) was produced.
  • Comparative Example 1 Aluminum alloys (I to M) having the compositions shown in Table 2 were melted and cast in the same manner as in Example 1. The resulting ingot was homogenized at 500 ° C. for 8 hours, and then the rolled surface was each milled by 8 mm. Then, hot rolling was started at 440 ° C., and hot rolling was terminated at 230 ° C. to obtain a hot rolled plate having a thickness of 5.0 mm. In Table 2, those outside the conditions of the present invention are underlined.
  • Comparative Example 2 An aluminum alloy (N) having the composition shown in Table 2 was melted and cast in the same manner as in Example 1. The obtained ingot was homogenized at 610 ° C. for 8 hours, and then hot as in Example 1. Rolling, cold rolling, and final annealing were performed to prepare a test material 14 (tempering: O material).
  • Example 3 shows the evaluation results of the number of intermetallic compound distributions and work hardening characteristics. In Table 3, those outside the conditions of the present invention are underlined. Evaluation of the number of intermetallic compound distributions: The number of intermetallic compound distributions having an equivalent circle diameter of 5 to 30 ⁇ m was quantified using a transmission electron microscope. The number of compounds was measured from the bright field image, and the number of compounds per unit volume ( ⁇ m 3 ) was calculated from the area of the measurement area and the sample thickness of the measurement area. The sample thickness was calculated from the product of the number of observed stripe patterns and the extinction distance using extinction stripes observed with a transmission electron microscope.
  • the aluminum alloy sheet of the present invention is hardened and hardened by cold pressing up to a working degree of about 70%, but processed by cold pressing with a working degree of 90% or more of the explosion-proof valve working area. It has material characteristics that make it hard to harden.
  • the thickness of the base plate before cold pressing is T0
  • the thickness after cold pressing is T1
  • the cold pressing degree R (%) [(T0 ⁇ T1) / T0] ⁇ 100, when comparing the tensile strength TS70 (MPa) when R is 70% and the tensile strength TS90 (MPa) when R is 90%, (TS70-TS90) is 5 MPa. It has characteristics that exceed.
  • Evaluation of the work hardening characteristics by the test material is performed by cold-rolling the test material at a workability of 70% and 90%, and performing a tensile test (JIS compliant) on the obtained cold-rolled material.
  • the difference between the tensile strength TS70 (MPa) and the tensile strength TS90 (MPa) with a workability of 90%, (TS70-TS90) was obtained, and those having a difference exceeding 5 MPa were evaluated as having characteristics that make it difficult to work harden. .
  • both test material 1-8 in accordance with the present invention are Al-Fe intermetallic compound equivalent circle diameter 5 ⁇ 30 nm are distributed 1,000 / [mu] m 3 or more in the matrix, cold Compared with the tensile strength TS70 at a workability of 70%, the tensile strength TS90 at a cold workability of 90% (explosion-proof valve working area) was reduced by 10 to 20 MPa, and it was difficult to work harden.
  • the test material 9 has a large amount of Si, it is inferior in the property of being hard to work and harden. Since the test material 10 has a small amount of Fe, the number of distributions of intermetallic compounds having an equivalent circle diameter of 5 to 30 ⁇ m is small, and the properties of being hard to work harden are inferior. Since the test material 11 has a large amount of Fe, a coarse intermetallic compound is generated, the work hardening is large, and the workability is inferior. Since the test material 12 has a large amount of Mn, it has poor properties that make it difficult to work and harden.
  • test material 13 Since the test material 13 has a large amount of Cu and Mn, the work hardening is large, the workability is inferior, and the properties that the work hardening is difficult are also inferior. Since the test material 14 has a high homogenization treatment temperature, the intermetallic compound is coarsened, and Fe is re-dissolved, and the characteristics that the work hardening is difficult due to the influence are inferior.

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  • Chemical & Material Sciences (AREA)
  • General Chemical & Material Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Electrochemistry (AREA)
  • Materials Engineering (AREA)
  • Engineering & Computer Science (AREA)
  • Inorganic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Sealing Battery Cases Or Jackets (AREA)

Abstract

L'invention porte sur un matériau de tôle d'alliage d'aluminium pour des boîtiers de batterie au lithium-ion, qui permet d'abaisser la pression de travail d'une soupape antidéflagrante et qui a une excellente aptitude au soudage au laser. Le matériau de tôle d'alliage d'aluminium pour des boîtiers de batterie au lithium-ion est caractérisé en ce qu'il contient, en % en masse, 0,5-2,0 % de Fe et 0,03-0,3 % de Si, tout en limitant le Cu, le Mn, le Mg et le Zn contenus en tant qu'impuretés, respectivement à une teneur inférieure ou égale à 0,10 %, le reste étant constitué d'Al et d'impuretés inévitables. Le matériau de tôle d'alliage d'aluminium pour des boîtiers de batterie au lithium-ion est également caractérisé en ce que : des composés intermétalliques d'Al-Fe ayant chacun un diamètre de cercle équivalent de 5-30 nm sont répartis dans la matrice à une densité supérieure ou égale à 1000 par µm3 ; et lorsque l'épaisseur de la plaque d'origine avant emboutissage à froid est représentée par T0, l'épaisseur après emboutissage à froid est représentée par T1, et le degré de réduction (R (%)) de l'emboutissage à froid est égal à [(T0 - T1)/T0] × 100, la différence entre la résistance à la traction au moment où R est de 70 % (TS70 (MPa)) et la résistance à la traction au moment où R est de 90 % (TS90 (MPa)), à savoir (TS70 - TS90), est supérieure à 5 MPa.
PCT/JP2011/065877 2011-07-12 2011-07-12 Matériau de tôle d'alliage d'aluminium pour des boîtiers de batterie au lithium-ion Ceased WO2013008314A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
PCT/JP2011/065877 WO2013008314A1 (fr) 2011-07-12 2011-07-12 Matériau de tôle d'alliage d'aluminium pour des boîtiers de batterie au lithium-ion
CN201180072252.XA CN103748245B (zh) 2011-07-12 2011-07-12 锂离子电池壳体用铝合金板材

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/JP2011/065877 WO2013008314A1 (fr) 2011-07-12 2011-07-12 Matériau de tôle d'alliage d'aluminium pour des boîtiers de batterie au lithium-ion

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CN103400945A (zh) * 2013-08-07 2013-11-20 舟山市新龙电子设备有限公司 圆柱形电容型锂离子电池的壳体
WO2014192256A1 (fr) * 2013-05-25 2014-12-04 株式会社Uacj Feuille d'alliage d'aluminium pour boîters de batterie, et procédé de fabrication de cette dernière
WO2019111970A1 (fr) * 2017-12-05 2019-06-13 日本軽金属株式会社 Plaque en alliage d'aluminium pour couvercle de batterie destinée à la formation de valve antidéflagrante d'un seul tenant, et procédé de fabrication de cette plaque en alliage d'aluminium
JP2020029601A (ja) * 2018-08-23 2020-02-27 日本軽金属株式会社 一体型防爆弁成形用の電池蓋用アルミニウム合金板およびその製造方法
WO2020039603A1 (fr) * 2018-08-23 2020-02-27 日本軽金属株式会社 Tôle d'alliage d'aluminium pour couvercle de batterie pour moulage de soupape antidéflagrante intégrée et son procédé de production
JP2020029599A (ja) * 2018-08-23 2020-02-27 日本軽金属株式会社 一体型防爆弁成形用の電池蓋用アルミニウム合金板およびその製造方法
JP2020029600A (ja) * 2018-08-23 2020-02-27 日本軽金属株式会社 一体型防爆弁成形用の電池蓋用アルミニウム合金板およびその製造方法
WO2020059160A1 (fr) * 2018-09-21 2020-03-26 日本軽金属株式会社 Tôle en alliage d'aluminium pour couvercle de batterie pour former une soupape de protection antidéflagrante intégrée et son procédé de production
WO2020059268A1 (fr) * 2018-09-21 2020-03-26 日本軽金属株式会社 Tôle d'alliage d'aluminium pour couvercle de batterie permettant de former une soupape antidéflagrante intégrée et son procédé de production
WO2020070944A1 (fr) * 2018-10-01 2020-04-09 日本軽金属株式会社 Plaque en alliage d'aluminium pour couvercle de batterie destinée à être utilisée pour mouler une valve antidéflagrante intégrée, et son procédé de production
JP2020056062A (ja) * 2018-10-01 2020-04-09 日本軽金属株式会社 一体型防爆弁成形用の電池蓋用アルミニウム合金板およびその製造方法
JP2020056063A (ja) * 2018-10-01 2020-04-09 日本軽金属株式会社 一体型防爆弁成形用の電池蓋用アルミニウム合金板およびその製造方法

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WO2017110869A1 (fr) * 2015-12-25 2017-06-29 株式会社Uacj Feuille en alliage d'aluminium pour corps de canette, et procédé de fabrication associé
CN106521246B (zh) * 2016-10-10 2018-01-02 上海华峰新材料研发科技有限公司 用于电池外壳铝合金防爆阀的材料及其制造方法
CN106566958B (zh) * 2016-11-11 2018-06-08 霍山飞翔汽车配件有限公司 一种高强度口琴管
CN106636767B (zh) * 2016-11-11 2018-07-10 霍山飞翔汽车配件有限公司 一种高性能口琴管
CN110106410B (zh) * 2019-04-22 2020-11-03 湖南工业大学 一种制备Al-Cu-Mg合金弹壳的冷冲工艺及其应用

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