WO2012169412A1 - 成形性、溶接性に優れた電池ケース用アルミニウム合金板 - Google Patents

成形性、溶接性に優れた電池ケース用アルミニウム合金板 Download PDF

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WO2012169412A1
WO2012169412A1 PCT/JP2012/063974 JP2012063974W WO2012169412A1 WO 2012169412 A1 WO2012169412 A1 WO 2012169412A1 JP 2012063974 W JP2012063974 W JP 2012063974W WO 2012169412 A1 WO2012169412 A1 WO 2012169412A1
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mass
aluminum alloy
eutectic
weldability
alloy plate
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PCT/JP2012/063974
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English (en)
French (fr)
Japanese (ja)
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鈴木　健太
堀　久司
圭治 金森
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日本軽金属株式会社
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Priority to KR1020137031814A priority Critical patent/KR101585309B1/ko
Priority to CN201280027984.1A priority patent/CN103608476B/zh
Publication of WO2012169412A1 publication Critical patent/WO2012169412A1/ja

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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
    • 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
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
    • 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
    • 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 a high-strength aluminum alloy plate excellent in formability and laser weldability, which is used for a secondary battery container such as a lithium ion battery.
  • Al-Mn 3000 series alloys are relatively excellent in strength, formability, and laser weldability, and are therefore used as materials for manufacturing secondary battery containers such as lithium ion batteries. Yes. After forming into a desired shape, it is hermetically sealed by laser welding and used with a secondary battery container. Development has been made on an aluminum alloy plate for a secondary battery container, which is based on an existing 3000 series alloy as well as the 3000 series alloy and has further improved strength and formability.
  • the composition of the aluminum alloy plate is as follows: Si: 0.10 to 0.60 mass%, Fe: 0.20 to 0.60 mass%, Cu: 0.10 to 0.70 mass%, Mn : 0.60 to 1.50 mass%, Mg: 0.20 to 1.20 mass%, Zr: more than 0.12 and less than 0.20 mass%, Ti: 0.05 to 0.25 mass%, B : 0.0010 to 0.02% by mass, comprising the balance Al and inevitable impurities, and having a 45 ° ear ratio of 4 to 7% in the rolling direction in the cylindrical container deep drawing method An aluminum alloy plate for rectangular cross-section battery containers is described.
  • Patent Document 2 Mn: 0.8% by mass or more, 1.8% by mass or less, Mg: more than 0.6% by mass and 1.2% by mass or less, Cu: more than 0.5% by mass, and 1.5% by mass %
  • Fe as an impurity is regulated to 0.5 mass% or less
  • Si is regulated to 0.3 mass% or less
  • the composition consists of the balance Al and inevitable impurities, and the ⁇ 001 ⁇ ⁇ 100> orientation
  • the ratio (C / S) of the orientation density C of ⁇ 123 ⁇ ⁇ 634> orientation is 0.65 or more and 1.5 or less
  • the tensile strength after the final cold rolling is 250 MPa or more and 330 MPa.
  • an aluminum alloy plate for a rectangular battery container having an elongation of 1% or more is described.
  • Patent Document 3 describes an aluminum alloy material for pulse laser welding and a battery case capable of preventing the occurrence of abnormal parts by pulse laser welding of an A1000 series aluminum material and forming a uniform good weld part. .
  • Ti which has been added to suppress the coarsening of crystal grains in the casting process, has an adverse effect on the welded portion, and an abnormal portion is formed when A1000 series aluminum is welded by pulse laser welding.
  • Ti contained in pure aluminum should be regulated to less than 0.01% by mass.
  • the 1000 series has a high elongation value, excellent formability, and the number of abnormal beads in laser welding is reduced, so that the weldability is stabilized. Therefore, as the size of the lithium ion battery increases, it is expected that high strength characteristics are also required, and it is conceivable to apply a relatively thick 1000 series aluminum plate as it is. Incidentally, in recent years, it has become common for a lithium ion battery container made of an aluminum alloy and its lid to be joined by pulse laser welding. As described above, a relatively thick 1000-series plate has excellent formability and a reduced number of abnormal beads, but may have good thermal conductivity. It is necessary to perform bonding under harsher conditions, for example, by increasing the energy.
  • the present invention has been devised to solve such problems, has a thickness applicable to a large-sized lithium ion battery container, has excellent moldability, and is also laser weldable.
  • An object of the present invention is to provide an excellent 1000 series aluminum alloy plate.
  • the aluminum alloy plate for battery case having excellent formability and weldability according to the present invention has Si: 0.01 to 0.4 mass%, Fe: 0.01 to 0.5 mass%. Co: 0.003 to 0.5% by mass, a component composition comprising the balance Al and inevitable impurities, and a metal structure having a number of second phase particles of 3 ⁇ m or more of less than 100 / mm 2 It is characterized by. Those having an elongation value of 30% or more are preferred.
  • the aluminum alloy plate of the present invention has high thermal conductivity, excellent formability, and excellent laser weldability, a secondary battery container with excellent sealing performance can be manufactured at low cost. Can do.
  • FIG. 1 is an Al—Co—Fe reaction diagram.
  • FIG. 2 is an Al—Co—Fe ternary phase diagram (liquid phase diagram).
  • FIG. 3 is a conceptual diagram illustrating a method for measuring / evaluating the number of welding defects.
  • Secondary batteries are manufactured by putting an electrode body in a container and then sealing it with a lid by welding or the like.
  • a secondary battery when charging, the temperature inside the container may rise and the pressure inside the container may increase. For this reason, if the strength of the material forming the container is low, there is a problem that the produced container is greatly swollen. Therefore, when a 1000 series aluminum alloy plate is selected as the material to be used, it is necessary to design a relatively thick container. Further, since a press method is generally used as a method for forming a container, the material itself is required to have excellent press formability.
  • a welding method is used as a method of sealing with a lid, it is also required to have excellent weldability.
  • a laser welding method is used as a welding method for manufacturing a secondary battery container or the like.
  • (1) stability of the weld bead width, stability of the penetration depth, and (2) suppression of generation of weld defects such as undercut and blowhole in the weld bead can be cited as problems.
  • the weld bead width is stable, and weld defects such as undercut and blowhole in the weld bead are reduced.
  • 1000 series aluminum alloy plates have good thermal conductivity, in order to perform pulsed laser welding of thick materials, the energy per pulse is increased, for example, under more severe conditions. Need to do.
  • the surface temperature of the weld bead during joining locally reaches a high temperature of 2000 ° C. or higher by irradiation with such a pulse laser.
  • Aluminum is considered to be a highly reflective material and reflects about 70% of the laser beam. Therefore, for example, intermetallic compounds such as Al 3 Fe and Al—Fe—Si, which originally existed near the surface of the aluminum alloy plate, have a color close to black, and therefore emit laser light more than ⁇ -Al. It is reasonable to think that it is easy to absorb and dissolves by heating first.
  • the irradiation time of one pulse of the pulse laser is a very short time of nanoseconds or femtoseconds.
  • the intermetallic compounds such as Al 3 Fe and Al—Fe—Si exposed on the surface of the weld bead are rapidly evaporated by evaporation. Inflates the volume.
  • the inventors of the present invention have made extensive studies to obtain an aluminum alloy plate excellent in laser weldability through investigation of the number of undercuts and blowholes that are excellent in press formability, as well as laser weldability, and reached the present invention. .
  • the contents will be described below.
  • Fe 0.01 to 0.5% by mass Since Fe is an element constituting Al 3 Fe, which is an intermetallic compound, it is desirable to reduce its content as much as possible in order to reduce welding defects. However, when the Fe content is less than 0.01% by mass, a high-purity aluminum ingot is used, which is not preferable because the cost cannot be increased. When the Fe content exceeds 0.5% by mass, a coarse intermetallic compound of Al 3 Fe crystallizes during ingot casting, and the formability in the final plate decreases, and these intermetallic compounds are Al during laser welding.
  • the Fe content is in the range of 0.01 to 0.5% by mass.
  • a more preferable Fe content is in the range of 0.01 to 0.4 mass%.
  • a more preferable Fe content is in the range of 0.02 to 0.4 mass%.
  • Si 0.01 to 0.4 mass% Si is an element that lowers the formability, and is easy to crystallize at the grain boundary as elemental Si, and is also an element that promotes crystallization of Al 6 Fe, which is a metastable phase. It is desirable to reduce its content as much as possible. However, when the Si content is less than 0.01% by mass, a high-purity aluminum ingot is used, and an increase in cost cannot be avoided. When the Si content exceeds 0.4% by mass, a coarse intermetallic compound of Al 6 Fe crystallizes during ingot casting, and simple Si is likely to crystallize at the grain boundaries, resulting in reduced formability in the final plate.
  • the Si content is in the range of 0.01 to 0.4 mass%.
  • a more preferable Si content is in the range of 0.01 to 0.3% by mass.
  • a more preferable Si content is in the range of 0.02 to 0.2% by mass.
  • Co 0.003 to 0.5 mass% Co is an extremely important element because it forms very fine eutectic Al 9 Co 2 clusters in the liquid phase of the solidifying slab.
  • clusters of the eutectic Al 9 Co 2 is generated earlier than the eutectic Al 3 Fe, it is believed to act as nuclei for the eutectic Al 3 Fe.
  • the initial Co / Fe concentration ratio is relatively large, eutectic Al 9 Co 2 crystallizes in the liquid phase of the solidifying slab with the clusters as nuclei, and the eutectic Al 3 Fe Crystallization is thermodynamically suppressed.
  • Co depends on the initial Co / Fe concentration ratio and the cooling rate during solidification
  • (1) the eutectic Al 3 Fe is refined by increasing the density of eutectic Al 3 Fe crystallization sites.
  • the Co content is less than 0.003 mass%, the above effects are not exhibited. If the Co content exceeds 0.5% by mass, the production cost simply increases, which is not preferable. Therefore, the Co content is in the range of 0.003 to 0.5 mass%. A more preferable Co content is in the range of 0.004 to 0.3% by mass. A more preferable Co content is in the range of 0.005 to 0.1% by mass.
  • the inventors have a transition element Co having a boiling point higher than that of Al, and by incorporating Co into a 1000 series aluminum alloy, for example, intermetallic compounds such as Al 3 Fe and Al—Fe—Si. It was assumed that a new intermetallic compound in which Fe, which is a transition element therein, was substituted with Co was generated as a metastable phase during casting solidification. And it was guessed that this new intermetallic compound that would have remained up to the final plate had a high boiling point and was difficult to vaporize during laser welding. However, the result of identification of the intermetallic compound by X-ray diffraction in the final plate completely denied this guess.
  • the eutectic temperature in the Al—Co based binary alloy system is 657 ° C.
  • the eutectic temperature in the Al—Fe based binary alloy system is 655 ° C.
  • the phase transformation of the Al—Co—Fe ternary alloy will be considered without considering the influence of other elements such as Si.
  • FIG. 2 shows the liquid phase surface of the Al—Co—Fe ternary system.
  • a eutectic reaction such as Al (L) ⁇ eutectic Al + Al 9 Co 2 occurs, and a eutectic structure composed of eutectic Al and Al 9 Co 2 is generated.
  • the composition Q in FIG. 2 schematically shows the case where the initial Co / Fe concentration ratio is 1, but the initial Co / Fe concentration ratio is smaller than 1, for example, 0.05.
  • the Co / Fe concentration ratio in the liquid phase after crystallization of the primary crystal ⁇ -Al gradually increases, but the (composition, temperature) of the liquid phase is the eutectic line ( It reaches the lower side (low temperature side) of Al (L) ⁇ eutectic Al + Al 9 Co 2 ). That is, even in the same supercooled state, eutectic Al 9 Co 2 is crystallized before eutectic Al 3 Fe.
  • eutectic Al 9 Co 2 is a very fine cluster at the initial stage of generation.
  • these clusters can be nuclei of the eutectic Al 3 Fe depending on the Co / Fe concentration ratio in the liquid phase. Therefore, the formation of fine eutectic Al 9 Co 2 clusters earlier in the supercooled state means homogeneous nucleation for eutectic Al 9 Co 2 , and in some cases for eutectic Al 3 Fe. It also means heterogeneous nucleation.
  • the eutectic Al 9 Co 2 clusters formed in the liquid phase are considered to act as homogeneous nuclei.
  • this cluster serves as a nucleus for eutectic Al within an appropriate initial concentration ratio of Co / Fe. 3 Fe crystallizes out, and as a result, eutectic Al 3 Fe is refined.
  • Co can be a refining agent for eutectic Al 3 Fe.
  • the number of second phase particles having a circle equivalent diameter of 3 ⁇ m or more in the metal structure is less than 100 particles / mm 2
  • the circle equivalent diameter in the metal structure is 3 ⁇ m.
  • the number of second phase particles above needs to be less than 100 particles / mm 2 . If it has such a metal structure, the existence density of intermetallic compounds such as Al 3 Fe, which is relatively coarse in terms of probability, becomes low, and welding defects such as undercuts and blowholes in laser welding bead Can be reduced.
  • the alloy composition range of the present invention by containing 0.003 to 0.5 mass% of Co, it becomes possible to achieve crystallization suppression and refinement of eutectic Al 3 Fe, which corresponds to a circle in the metal structure.
  • the number of second phase particles having a diameter of 3 ⁇ m or more can be less than 100 particles / mm 2 .
  • Cold-rolled annealed material When applying a 1000 series aluminum alloy plate to a large-sized lithium ion battery container or the like at an elongation value of 30% or more, it has not only excellent laser weldability but also excellent formability. is necessary. The formability of the material can be known from the value of elongation during the tensile test. The details will be given in the description of Examples described later. As the 1000 series aluminum alloy plate of the present invention applied to a large-sized lithium ion battery container or the like, those having a characteristic that the elongation value is 30% or more are suitable.
  • the molten aluminum alloy melted in the melting furnace may be cast after it is once transferred to the holding furnace, but may be cast directly from the melting furnace.
  • a more desirable sedation time is 45 minutes or more.
  • in-line degassing or filtering may be performed.
  • In-line degassing is mainly of a type in which an inert gas or the like is blown into a molten aluminum from a rotating rotor, and hydrogen gas in the molten metal is diffused and removed in bubbles of the inert gas.
  • nitrogen gas is used as the inert gas, it is important to control the dew point to, for example, ⁇ 60 ° C. or lower.
  • the amount of hydrogen gas in the ingot is preferably reduced to 0.20 cc / 100 g or less.
  • the amount of hydrogen gas in the ingot is large, porosity is generated in the final solidified portion of the ingot. Therefore, the reduction rate per pass in the hot rolling process is restricted to, for example, 7% or more, and the porosity is crushed. There is a need.
  • hydrogen gas that is supersaturated in the ingot is deposited during laser welding after forming the final plate, depending on the conditions of the homogenization treatment before the hot rolling process, and a large number of blown gases are blown into the beads. In some cases, holes are generated. For this reason, the more preferable amount of hydrogen gas in the ingot is 0.15 cc / 100 g or less.
  • the cast ingot is manufactured by semi-continuous casting (DC casting).
  • DC casting semi-continuous casting
  • the solidification cooling rate at the center portion of the ingot is about 1 ° C./sec.
  • a relatively coarse intermetallic compound such as Al—Fe—Si is crystallized from the molten aluminum alloy at the center of the ingot.
  • the casting speed in semi-continuous casting depends on the width and thickness of the ingot, it is usually 50 to 70 mm / min in consideration of productivity.
  • the flow rate of molten aluminum depends on the degassing conditions such as the flow rate of the inert gas. The smaller the (supply amount), the better the degassing efficiency in the tank, and it is possible to reduce the amount of hydrogen gas in the ingot.
  • a more desirable casting speed is 30 to 40 mm / min.
  • productivity is lowered, which is not desirable.
  • the casting speed is slower, the slope of the sump (solid phase / liquid phase interface) in the ingot becomes gentler, and casting cracks can be prevented.
  • Homogenization treatment is performed on an ingot obtained by casting by a semi-continuous casting method at 420 to 620 ° C. for 1 hour or longer .
  • the homogenization process is a process in which the ingot is kept at a high temperature to facilitate rolling, and casting segregation and elimination of residual stress inside the ingot are performed.
  • it is necessary to hold at a holding temperature of 420 to 620 ° C. for 1 hour or longer.
  • it is also a process for dissolving the transition elements constituting the intermetallic compound crystallized during casting to some extent in the matrix.
  • a more preferable homogenization temperature is 420 to 600 ° C.
  • the ingot held at a high temperature for a predetermined time in the hot rolling process is suspended by a crane after homogenization and brought to the hot rolling mill. Depending on the type of hot rolling mill, it is usually several times.
  • the sheet is hot-rolled by such a rolling pass and wound on a roll as a hot-rolled sheet having a predetermined thickness, for example, about 4 to 8 mm.
  • the roll on which the hot rolled sheet is wound is passed through a cold rolling machine and usually subjected to several passes of cold rolling.
  • an intermediate annealing treatment is performed as necessary.
  • the intermediate annealing is also a softening treatment, but depending on the material, a cold rolling roll may be inserted into the batch furnace and kept at a temperature of 300 to 450 ° C. for 1 hour or longer.
  • the holding temperature is lower than 300 ° C., softening is not promoted, and when the holding temperature exceeds 450 ° C., the processing cost increases.
  • the intermediate annealing can also serve as a solution treatment if it is kept within a temperature of 400 ° C. to 550 ° C. within 15 seconds by a continuous annealing furnace and then rapidly cooled.
  • the holding temperature is lower than 400 ° C., softening is not promoted, and when the holding temperature exceeds 550 ° C., there is a risk of swelling.
  • the final annealing performed after the final cold rolling may be, for example, a batch process in which an annealing furnace is maintained at a temperature of 300 to 500 ° C. for 1 hour or longer. If it is kept at a temperature of 550 ° C. within 15 seconds and then cooled rapidly, it can also serve as a solution treatment.
  • final annealing is not necessarily essential in the present invention, but it is desirable that the final plate has a certain degree of elongation in consideration of formability in normal DI molding. Considering the moldability in the mold forming process, it is desirable to use an annealed material or a solution treated material. When the mechanical strength is prioritized over the moldability, it is provided as a cold rolled material.
  • the final cold rolling rate is preferably in the range of 50 to 90%. If the final cold rolling rate is within this range, the average recrystallized grains in the final plate after annealing can be set to 20 to 100 ⁇ m, the elongation value can be 30% or more, and the appearance skin after molding can be finished beautifully. be able to. A more preferable final cold rolling rate is in the range of 60 to 90%. On the other hand, the final cold rolling rate when the material is cold rolled without being subjected to final annealing is preferably in the range of 5 to 40%. If the ironing process increases during DI molding, it is necessary to provide a final plate that is slightly harder than the annealed material. A more preferable final cold rolling rate is in the range of 10 to 30%. An aluminum alloy plate for a secondary battery container can be obtained through the normal steps as described above.
  • the ingot was chamfered by 2 mm on each side after cutting the hot water to a thickness of 26 mm.
  • This ingot is inserted into an electric heating furnace, heated to 430 ° C. at a temperature rising rate of 100 ° C./hr, homogenized at 430 ° C. ⁇ 1 hour, and subsequently heated to a thickness of 6 mm with a hot rolling mill. It hot-rolled until it became.
  • the cold-rolled annealed plate was cold-rolled without subjecting the hot-rolled plate to intermediate annealing to obtain a 1 mm cold-rolled plate.
  • the final cold rolling rate in this case was 83%.
  • the cold-rolled sheet was inserted into the annealer, and after annealing at 390 ° C. for 1 hour, the cold-rolled sheet was taken out from the annealer and air-cooled.
  • each sample material thus obtained was evaluated for formability and laser weldability.
  • Evaluation of formability Evaluation of formability of the obtained final plate was performed by elongation (%) of a tensile test. Specifically, a JIS No. 5 test piece is collected so that the tensile direction is parallel to the rolling direction, and a tensile test is performed according to JISZ2241, to obtain tensile strength, 0.2% proof stress, and elongation (breaking elongation). It was. In the final plate that was annealed after cold rolling, the test material having an elongation value of 30% or more was considered as good formability ( ⁇ ), and the test material that was less than 30% was considered as poor formability ( ⁇ ). did. The evaluation results are shown in Table 2.
  • the final plate obtained was subjected to pulsed laser irradiation to evaluate laser weldability.
  • YAG laser welder JK701 manufactured by LUMONICS frequency 37.5Hz, welding speed 400mm / min, energy per pulse 9.0J, pulse width 1.5msec, shield gas (nitrogen) flow rate 1.5 (L / min )
  • Two plates of the test material were butted without gaps between the ends, and pulse laser welding having a total length of 100 mm was performed along the portion.
  • a black defect portion was detected by image editing software, and the area of the black portion defect was calculated by image analysis software.
  • the number of particles corresponding to each equivalent circle diameter was calculated from the black part defect area.
  • a test material in which the number of black part defects having an equivalent circle diameter of 0.4 mm or more was less than 10 was evaluated as good ( ⁇ ) in the number of weld defects, and a black part having an equivalent circle diameter of 0.4 mm or more.
  • the test material in which the number of defects was 10 or more was determined as poor weld defect number evaluation (x). The evaluation results are shown in Table 2.
  • the test materials of Examples 1 to 7 are within the range of the alloy composition of the present invention, and the number of welding defects sufficiently satisfies the standard of less than 10, so that the laser weldability is excellent. Yes. Moreover, since the elongation value in the tensile test is 30% or more, the moldability is also excellent.
  • the sample material of Comparative Example 1 has an extremely low Co content of 0.0001% by mass, 12 welding defects, and is inferior in laser weldability.
  • the sample material of Comparative Example 2 has a low Co content of 0.0005% by mass, has 12 welding defects, and is inferior in laser weldability.
  • the sample material of Comparative Example 3 has a low Co content of 0.0008% by mass, 11 welding defects, and is inferior in laser weldability.
  • the specimen of Comparative Example 4 has a high Fe content of 0.70% by mass, 24 weld defects, and is inferior in laser weldability.
  • the sample material of Comparative Example 5 has a high Si content of 0.42% by mass, the number of welding defects is 17, and is inferior in laser weldability.
  • the sample material of Comparative Example 6 has a high Si content of 0.65% by mass, has 10 welding defects, and is inferior in laser weldability.
  • the number of second phase particles having an equivalent circle diameter of 3 ⁇ m or more was less than 100 / mm 2 in comparison with Examples 1 to 7.
  • the existence density of intermetallic compounds such as coarse Al 3 Fe was considered low, and the evaluation was good ( ⁇ ).
  • the number of second phase particles having an equivalent circle diameter of 3 ⁇ m or more is 100 particles / mm 2 or more, and the presence density of relatively coarse intermetallic compounds such as Al 3 Fe is high. It was thought that it was poor evaluation (x).
  • the evaluation results of the image analysis of the second phase particles in these metal structures agree with the above-described evaluation results of the laser weldability.
  • a 1000 series aluminum alloy plate having a thickness applicable to a large-sized lithium ion battery container, excellent in formability, and excellent in laser weldability.

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PCT/JP2012/063974 2011-06-07 2012-05-30 成形性、溶接性に優れた電池ケース用アルミニウム合金板 WO2012169412A1 (ja)

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KR1020137031814A KR101585309B1 (ko) 2011-06-07 2012-05-30 성형성, 용접성이 우수한 전지 케이스용 알루미늄 합금판
CN201280027984.1A CN103608476B (zh) 2011-06-07 2012-05-30 成型性、焊接性优异的电池外壳用铝合金板

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JP2011127136 2011-06-07
JP2011-127136 2011-06-07
JP2012-102188 2012-04-27
JP2012102188A JP5846032B2 (ja) 2011-06-07 2012-04-27 成形性、溶接性に優れた電池ケース用アルミニウム合金板

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CN103608476A (zh) 2014-02-26
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