WO2013118734A1 - Aluminum alloy sheet for connecting components and manufacturing process therefor - Google Patents

Aluminum alloy sheet for connecting components and manufacturing process therefor Download PDF

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Publication number
WO2013118734A1
WO2013118734A1 PCT/JP2013/052630 JP2013052630W WO2013118734A1 WO 2013118734 A1 WO2013118734 A1 WO 2013118734A1 JP 2013052630 W JP2013052630 W JP 2013052630W WO 2013118734 A1 WO2013118734 A1 WO 2013118734A1
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aluminum alloy
mass
heat treatment
alloy plate
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PCT/JP2013/052630
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French (fr)
Japanese (ja)
Inventor
増田　哲也
高木　康夫
貴彦 中村
光雄 日野
Original Assignee
株式会社神戸製鋼所
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Priority claimed from JP2012277037A external-priority patent/JP5330590B1/en
Priority claimed from JP2012277036A external-priority patent/JP5647665B2/en
Application filed by 株式会社神戸製鋼所 filed Critical 株式会社神戸製鋼所
Priority to EP13746696.7A priority Critical patent/EP2813592B1/en
Priority to CN201380008239.7A priority patent/CN104093868B/en
Priority to KR1020147022028A priority patent/KR101600224B1/en
Publication of WO2013118734A1 publication Critical patent/WO2013118734A1/en

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    • 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
    • C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
    • 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
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium 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
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
    • H01B1/00—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors
    • H01B1/02—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors mainly consisting of metals or alloys
    • H01B1/023—Alloys based on aluminium
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
    • H01B13/00—Apparatus or processes specially adapted for manufacturing conductors or cables

Definitions

  • the present invention electrically connects between electric devices (batteries, inverters, motors, etc.) mounted on various electric transportation devices using electricity as a power source such as an electric vehicle or between components inside the electric device.
  • the present invention relates to an aluminum alloy plate for connecting parts used for connecting parts to be connected and a method for manufacturing the same.
  • Various electric devices such as a battery group, an inverter, and a motor are mounted on various electric transport devices (hybrid vehicle, fuel cell vehicle, electric locomotive, etc.) that use electricity as a power source including an electric vehicle.
  • a connecting component called a bus-bar is used.
  • connection component Since this connection component must conduct electricity, it is naturally necessary to have excellent conductivity. Further, when the connecting part is connected by a connecting tool such as a bolt, deformation (creep deformation) of the connecting part 1a (see FIG. 1) of the connecting part 1 occurs due to heat generation when energized, so that the tightening torque of the connecting tool is increased.
  • the connecting parts must have a high creep resistance so that they do not drop and the couplings come loose or come off.
  • the connecting component is often designed in a shape having a curved portion with a small bending radius (R). Therefore, the connection component needs to be excellent in bending workability.
  • Patent Document 1 discloses an aluminum alloy for connection parts in which the component composition is specified and the conditions of conductivity and tempering are specified. Patent Document 1 describes that the aluminum alloy has excellent conductivity and excellent creep resistance.
  • Patent Document 2 discloses a method for producing an aluminum alloy sheet in which a homogenized heat treatment, hot rolling, cold rolling, and final annealing under predetermined conditions are performed on an ingot with a specified component composition. And in patent document 2, it describes that the aluminum alloy plate manufactured with the said manufacturing method has the bending workability requested
  • Patent Documents 3 and 4 disclose a technique related to an aluminum alloy plate for an automobile panel, not for a connection part, in order to improve the bending workability of an Al—Mg—Si based alloy (JIS6000 based Al alloy).
  • a technique in which the texture is controlled to set the Cube orientation distribution density to a predetermined value (Patent Document 3) or a crystal grain having an orientation difference of 20 ° or less with respect to the total grain boundary length between all crystal grains.
  • Patent Document 4 is disclosed.
  • Patent Document 1 is a technique that focuses on the improvement of creep resistance, it is a technique that does not consider bending workability at all (see paragraph 0010 of Patent Document 1). Naturally, the bending workability required for the connecting parts could not be satisfied. Therefore, when the technique disclosed in Patent Document 1 is applied to a connection part, a bending crack may occur on the surface during molding.
  • Patent Document 2 is a technique that focuses on the improvement of bending workability, it is a technique that does not consider creep resistance at all (see paragraph 0001 and the like in Patent Document 2). Of course, the creep resistance required for the connecting parts could not be satisfied. Therefore, when the technique disclosed in Patent Document 2 is applied to a connection component, a connecting portion 1a (see FIG. 1) of the connection component 1 is deformed by heat generated during energization, so that a bolt or the like for connecting the connection component can be obtained. There is a possibility that the connector will loosen or come off.
  • Patent Documents 3 and 4 consider bending workability as well as Patent Document 2, but do not consider creep resistance at all, and are not for connecting parts. It is a technology for automobile panels. Therefore, the techniques disclosed in Patent Documents 3 and 4 do not satisfy the creep resistance required for connecting parts. Furthermore, even if it has the bending workability required for an automobile panel having a plate thickness of about 1 mm, the connecting part usually has a plate thickness of about 2 mm, so that it has a high bending workability as required for the connecting part. Hard to think.
  • the aluminum alloy plate has both the creep resistance and the bending workability required for the connecting part while maintaining the conductivity that is an essential characteristic for the connecting part. No technology seems to exist. In addition, this situation is technical common sense (in order to improve the creep resistance of a plate made of metal, it is necessary to improve the strength, but if the strength is improved, the bending workability of the plate will be reduced, that is, The creep resistance and the bending workability are in a trade-off relationship) and have been considered as a matter of course.
  • an object of the present invention is to provide an aluminum alloy plate for connection parts that is excellent in creep resistance and bending workability while maintaining conductivity, and a method for manufacturing the same.
  • the inventors of the present invention show that the Cube orientation distribution density and the component composition on the surface of the aluminum alloy plate for connecting parts have a great influence on the creep resistance and bending workability. And found the present invention.
  • the aluminum alloy plate for connecting parts according to the present invention contains Si: 0.3 to 1.5 mass%, Mg: 0.3 to 1.0 mass%, and the balance is made of Al and inevitable impurities. It is made of an aluminum alloy, has an electric conductivity of 45.0% IACS or more, and a Cube orientation distribution density on the plate surface by a crystal orientation distribution function analysis of 15 or more.
  • the creep resistance can be improved and the bending workability can be improved. That is, according to the aluminum alloy plate for connecting parts, both creep resistance and bending workability required for the connecting parts can be achieved. Moreover, according to this aluminum alloy plate for connection parts, since the content of Si and Mg is specified within a predetermined range, the effect of improving creep resistance can be ensured. Furthermore, according to this aluminum alloy plate for connection parts, since the electrical conductivity is specified to be 45.0% IACS or more, the electrical conductivity required for the connection parts can be ensured.
  • the aluminum alloy plate for connection parts according to the present invention preferably includes Fe: less than 0.5 mass% and Zn: less than 0.5 mass% among the inevitable impurities.
  • the content of Fe and Zn among inevitable impurities is specified to be less than a predetermined value, so that the effect of improving the bending workability can be ensured. it can.
  • the aluminum alloy plate for connecting parts contains Cu: less than 1.0% by mass, Mn: less than 1.0% by mass, Cr: less than 0.5% by mass, Zr: 0.0. It is preferable to further contain one or more selected from less than 3% by mass and Ti: less than 0.1% by mass.
  • this aluminum alloy plate for connecting parts since it further contains one or more selected from Cu, Mn, Cr, Zr, Ti less than a predetermined value, while ensuring the effect of improving the bending workability, The effect of improving the creep resistance can be further ensured.
  • the method for producing an aluminum alloy plate for connecting parts comprises a homogenization heat treatment step of subjecting an ingot made of the aluminum alloy to a homogenization heat treatment at 500 to 570 ° C. for 1 to 24 hours, and the homogenization heat treatment.
  • a solution heat treatment step of applying an artificial aging treatment to the hot-rolled sheet subjected to the solution heat treatment.
  • the component composition of the aluminum alloy to be used is specified, the conditions for the homogenization heat treatment and the solution heat treatment are specified, and the cold rolling is not performed.
  • the electrical conductivity, the Cube orientation distribution density on the surface of the plate, and the proof stress of the aluminum alloy plate for connection parts manufactured by the method can be set to a predetermined value or more.
  • the Cube orientation distribution density on the plate surface by the crystal orientation distribution function analysis is 20 or more, and the average crystal grain size in the rolling direction on the plate surface is 150 ⁇ m or less. Bending surface quality can be improved by reducing the crystal grain size.
  • the method for producing an aluminum alloy plate for connecting parts comprises a homogeneous heat treatment step of subjecting an ingot made of the aluminum alloy to a homogenization heat treatment at 500 to 570 ° C. for 1 to 24 hours, and the homogenization heat treatment.
  • the component composition of the aluminum alloy to be used is specified, the conditions for the homogenization heat treatment, hot rolling and solution heat treatment are specified, and cold rolling is not performed.
  • the electrical conductivity, the Cube orientation distribution density and the proof stress of the aluminum alloy plate for connecting parts manufactured by the manufacturing method can be set to a predetermined value or more and the crystal grain size can be set to a predetermined value or less.
  • the conductivity, the Cube orientation distribution density of the plate surface is specified as a predetermined value or more, and the contents of Si and Mg are specified in a predetermined range. Since it retains conductivity and is excellent in creep resistance and bending workability, it can be suitably used as a connection part.
  • the composition of the aluminum alloy to be used is specified, the conditions for the homogenization heat treatment and the solution heat treatment are specified, and cold rolling is not performed. As a result, it is possible to produce an aluminum alloy plate for connecting parts that is excellent in creep resistance and bending workability while maintaining conductivity.
  • connection component bus bar
  • connection component bus bar
  • FIG. 1 It is a perspective view of the connection component (bus bar) concerning the embodiment of the present invention. It is a flowchart of the manufacturing method of the aluminum alloy plate for connection components which concerns on this invention. It is a schematic diagram explaining the method of the bending test in the Example of this invention.
  • An aluminum alloy plate for connecting parts according to the present invention contains a predetermined amount of Si and Mg, and the balance is made of an aluminum alloy composed of Al and inevitable impurities, and has a conductivity, And the Cube orientation distribution density on the plate surface is a predetermined value or more.
  • the aluminum alloy plate for connecting parts according to the present invention preferably has Fe and Zn of unavoidable impurities less than a predetermined value, and is selected from Cu, Mn, Cr, Zr, and Ti that are less than a predetermined value. More preferably, it contains seeds or more.
  • Si forms aging precipitates together with Mg during the artificial aging treatment after solution heat treatment. Since Si inhibits the movement of dislocations in a high temperature environment and improves creep resistance, Si is an essential element for the aluminum alloy plate for connecting parts according to the present invention. If the Si content is less than 0.3% by mass, desired creep resistance cannot be obtained. On the other hand, when the Si content exceeds 1.5% by mass, coarse crystallized substances and precipitates are formed, and particularly bending workability is deteriorated. Therefore, the Si content is 0.3 to 1.5% by mass. In order to ensure the effect of improving the bending workability and creep resistance, the Si content is preferably 0.4 to 1.5% by mass, preferably 0.5 to 1.3% by mass. % Is more preferable.
  • Mg forms an aging precipitate during the artificial aging treatment after solution heat treatment with Si. Since Mg inhibits the movement of dislocations under a high temperature environment and improves creep resistance, Mg is an essential element for the aluminum alloy plate for connecting parts according to the present invention. If the Mg content is less than 0.3% by mass, desired creep resistance cannot be obtained. On the other hand, when the Mg content exceeds 1.0% by mass, coarse crystallized substances and precipitates are formed, and bending workability is particularly deteriorated. Therefore, the Mg content is 0.3 to 1.0 mass%. The Mg content is preferably 0.5 to 0.8% by mass in order to ensure the effect of improving bending workability and creep resistance.
  • Fe, Zn, or the like may be contained within a range that does not hinder the effects of the present invention.
  • Fe and Zn are each preferably less than 0.50% by mass (restricted to less than 0.50% by mass). This is because if the Fe content or Zn content is 0.50% by mass or more, the bending workability or the corrosion resistance is lowered.
  • Fe and Zn are contained to some extent in scrap and recycled metal (for example, scraps of aluminum alloy materials for clad materials such as brazing sheets). The recycled metal can be blended so that the content of Fe and Zn in the aluminum alloy plate is less than the above range, and the raw material cost can be reduced.
  • elements other than Fe and Zn may be contained as unavoidable impurities to the extent that the effects of the present invention are not hindered.
  • Cu less than 1.00% by mass
  • Cu accelerates aging precipitate formation in the artificial aging treatment after the solution heat treatment. By inhibiting the movement of dislocations in a high temperature environment, Cu improves creep resistance. In order to acquire the said effect, it is preferable to contain Cu 0.05 mass% or more. On the other hand, if the Cu content is 1.00% by mass or more, the stress corrosion cracking resistance, weldability, and bending workability are remarkably deteriorated. Therefore, when Cu is contained in the aluminum alloy plate, the Cu content is less than 1.00% by mass.
  • Mn (Mn: less than 1.00% by mass) Mn generates dispersed particles (dispersed phase) during the homogenization heat treatment, and these dispersed particles hinder grain boundary movement after recrystallization. Therefore, Mn is an element that has an effect of refining crystal grains.
  • the bending workability of the aluminum alloy plate for connection parts according to the present invention improves as the crystal grains of the aluminum alloy structure become finer. In order to acquire the said effect, it is preferable to contain 0.01 mass% or more of Mn.
  • the Mn content is 1.00% by mass or more, a coarse Al—Fe—Si—Mn-based crystallized product is likely to be formed during melting and casting, which causes a decrease in bending workability. Therefore, when Mn is contained in the aluminum alloy plate, the Mn content is less than 1.00% by mass.
  • Cr is an element that has an effect of refining crystal grains. In order to acquire the said effect, it is preferable to contain 0.01 mass% or more of Cr. On the other hand, if the Cr content is 0.50% by mass or more, a coarse intermetallic compound is likely to be produced during melting and casting, and the bending workability is deteriorated. Therefore, when Cr is contained in the aluminum alloy plate, the Cr content is less than 0.50% by mass.
  • Zr is an element that has an effect of refining crystal grains. In order to acquire the said effect, it is preferable to contain Zr 0.01 mass% or more. On the other hand, when the Zr content is 0.30 mass% or more, a coarse intermetallic compound is likely to be produced during melting and casting, and bending workability is deteriorated. Therefore, when Zr is contained in the aluminum alloy plate, the content of Zr is less than 0.30% by mass.
  • Ti is an element having the effect of making the crystal grains of the ingot finer and improving the bending workability by containing a small amount of Ti. In order to acquire the said effect, it is preferable to contain Ti 0.01 mass% or more. On the other hand, if the Ti content is 0.10% by mass or more, a coarse compound is formed and bending workability is deteriorated. Therefore, when Ti is contained in the aluminum alloy plate, the Ti content is less than 0.10% by mass.
  • the electrical conductivity of the aluminum alloy plate for connecting parts according to the present invention is 45.0% IACS or more.
  • the electrical conductivity is 45.0% IACS or more, electrical conductivity as a connected device can be ensured.
  • the electrical resistance is high, that is, the conductivity is less than 45.0% IACS, it is necessary to increase the cross-sectional area of the connecting component in order to flow a desired current, leading to an increase in the component weight.
  • the conductivity is preferably as high as possible, preferably 47.0% IACS or more, and more preferably 50.0% IACS or more.
  • the adjustment of conductivity is achieved by controlling the Si content, Mg content, homogenization heat treatment conditions, solution heat treatment conditions, and artificial aging conditions in the aluminum alloy sheet manufacturing process.
  • the conductivity is preferably 60% IACS or less.
  • the Cube orientation distribution density on the surface of the aluminum alloy plate for connection parts according to the present invention is 15 or more.
  • the Cube orientation distribution density on the plate surface is 15 or more, both creep resistance and bending workability required for the connecting parts can be achieved.
  • the Cube orientation distribution density on the surface of the plate is less than 15, bending workability is deteriorated.
  • the Cube orientation distribution density is preferably 20 or more, more preferably 30 or more, in order to ensure the effect of improving creep resistance and bending workability.
  • the Cube orientation distribution density is less than 15, which indicates that the crystal orientation of the plate surface is relatively random.
  • the Cube orientation distribution density is 15 or more, that is, when the Cube orientation is accumulated more than a certain amount, the ratio of small-angle grain boundaries having a small orientation difference between adjacent crystal grains increases. Reduce or eliminate grain boundary step during deformation.
  • the Cube orientation since a uniform slip deformation is possible compared to other orientations, formation of a shear band is suppressed.
  • the bending workability is improved by setting the Cube orientation distribution density to 15 or more. Can improve (improve). If the Cube orientation distribution density is excessively increased, the manufacturing conditions become severe and the productivity is lowered. Therefore, the Cube orientation distribution density is preferably 100 or less.
  • the Cube orientation distribution density is defined by the Cube orientation distribution density by crystal orientation distribution function analysis (hereinafter, referred to as ODF analysis as appropriate) with more accurate crystal texture measurement accuracy.
  • ODF analysis crystal orientation distribution function analysis
  • the Cube orientation distribution density by ODF analysis can express a wide range quantitatively because the Cube orientation is represented by a ratio (dimensionalless) from a random orientation (non-oriented Al powder sample of a standard sample).
  • the in-plane (100 plane) rotational orientation cannot be separated, only a pure Cube orientation cannot be extracted.
  • Cube orientation distribution density on the surface of the aluminum alloy plate by ODF analysis is measured using, for example, an X-ray diffractometer [model “Rigaku RAD-rX” (Ru-200B)] manufactured by Rigaku Corporation. This is done by measuring the plate surface.
  • the X-ray diffractometer can perform ODF analysis with an incomplete pole figure. That is, incomplete pole figures of ⁇ 100 ⁇ plane and ⁇ 111 ⁇ plane are created by schluz reflection method, ODF analysis is performed by applying Bunge's iterative series expansion method (positivity method), and Cube orientation distribution density Can be requested.
  • the relationship between the bending direction and the Cube orientation (orientation direction) when bending the aluminum alloy plate is set so that the Cube orientation of the plate is parallel to the bending direction of the plate (the bending direction of the plate is the material plate).
  • the Cube orientation during deformation becomes stable, and good bending workability is obtained. Since the Cube orientation of the plate has the same structure even when rotated 90 degrees, there is no distinction between 0 degrees and 90 degrees. For this reason, even if the bending direction of the plate is parallel or perpendicular to the rolling direction of the material plate, the Cube orientation has the same structure, and good bending workability can be obtained.
  • the Cube orientation (distribution direction) of the plate, such as the rolling direction of the plate being 45 degrees with the bending direction of the plate, the Cube orientation is being deformed. Since the crystal orientation is randomized and the bending workability may be inferior, it is preferable that the bending direction of the plate when bending is the above two directions.
  • the adjustment of the Cube orientation distribution density on the surface of the plate is achieved by the Si content, the Mg content, the hot rolling conditions in the manufacturing process of the aluminum alloy plate, and the absence of cold rolling. .
  • the proof stress (0.2% proof stress) of the aluminum alloy plate for connecting parts according to the present invention is preferably 180 MPa or more.
  • the yield strength is preferably 190 MPa or more, and more preferably 195 MPa or more.
  • the adjustment of the proof stress is achieved by the Si content, the Mg content, the homogenization heat treatment condition, the solution treatment condition and the artificial aging treatment condition in the production process of the aluminum alloy sheet.
  • connection component is a component that electrically connects a plurality of members. Specifically, it is a bus bar that is electrically connected to various electric devices such as battery groups, inverters, motors, etc. is there. And although a bus bar is not specifically limited about a shape, while it has predetermined thickness, it is a component which exhibits plate shape or a square material shape. For example, the bus bar is a component having a shape as shown in FIG.
  • the bus bar made of aluminum alloy has to have a larger cross-sectional area than the bus bar made of copper in order to ensure the conductive performance.
  • the bus bar made of aluminum alloy has to have a larger cross-sectional area than the bus bar made of copper in order to ensure the conductive performance.
  • the aluminum alloy plate for connection parts according to the present invention is preferably applied to a bus bar having a thickness of 1.5 mm or more, particularly 1.8 to 5.0 mm, among the connection parts, and has a remarkable effect ( Effect of achieving both creep resistance and bending workability).
  • the method for producing an aluminum alloy plate for connecting parts includes a homogenization heat treatment step S2, a hot rolling step S3, a solution heat treatment step S4, and an artificial aging treatment step S5. .
  • a homogenization heat treatment step S2 a hot rolling step S3, a solution heat treatment step S4, and an artificial aging treatment step S5. .
  • the respective steps will be mainly described.
  • the aluminum alloy having the above component composition is melted, cast by a known casting method such as a DC forging method, and cooled to below the solidus temperature of the aluminum alloy, and cast to a thickness of about 400 to 600 mm. Make a lump and chamfer as necessary.
  • homogenization heat treatment process In the homogenization heat treatment step S2, homogenization heat treatment (soaking) is performed at a predetermined temperature before rolling the ingot cast in the casting step S1. By subjecting the ingot to homogenization heat treatment, internal stress is removed, solute elements segregated at the time of casting are homogenized, and intermetallic compounds precipitated at the time of casting cooling and thereafter grow. Further, the homogenization heat treatment also serves as preheating for the subsequent hot rolling step S3.
  • the heat treatment temperature (ingot temperature) in the homogenization heat treatment step S2 is 500 to 570 ° C.
  • the heat treatment time (holding time) in the homogenization heat treatment step S2 may be 1 hour or longer in order to complete the homogenization, and may be within 24 hours from the viewpoint of production efficiency.
  • the homogenized ingot is hot-rolled continuously from the homogenizing heat treatment step S2.
  • the temperature at the time of completion of the heat treatment in the homogenization heat treatment step S2 is maintained, the ingot is roughly rolled, and further, hot rolled plate (hot coil) having a desired thickness is obtained by finish rolling.
  • the thickness of the hot rolled sheet may be set by calculating back from the final thickness of the aluminum alloy sheet.
  • the Cube orientation distribution density can be controlled by the hot rolling end temperature.
  • the hot rolling end temperature should be 360 ° C. or less, and recrystallization is suppressed even at the end of hot rolling, and the processed structure remains.
  • the temperature is 330 ° C. or lower.
  • the hot rolled plate manufactured in the hot rolling step S3 is solution heat treated.
  • the heat treatment temperature (ingot temperature) in the solution heat treatment step S4 is 500 to 570 ° C.
  • the heat treatment temperature is less than 500 ° C., undissolved Si or Mg remains, so that an appropriate precipitate distribution cannot be obtained after solution heat treatment and artificial aging treatment, and desired proof stress and creep resistance can be obtained. I can't.
  • it exceeds 570 ° C. local melting (burning) occurs on the plate surface. More preferably, it is 520 to 550 ° C.
  • the holding time at the heat treatment temperature in the solution heat treatment step S4 is within 60 seconds (may be 0 seconds).
  • the rate of temperature increase from 200 ° C. to the heat treatment temperature is preferably 5 ° C./s or more, and the rate of temperature decrease from the heat treatment temperature to 200 ° C. is 10 ° C./s or more. preferable.
  • the artificial aging treatment is performed at a predetermined temperature and a predetermined time on the hot-rolled sheet subjected to the solution heat treatment in the solution heat treatment step S4.
  • the heat treatment temperature in the artificial aging treatment step S5 is not particularly limited, but is preferably 150 to 250 ° C. When the temperature is lower than 150 ° C., desired proof stress and creep resistance cannot be obtained, and when the temperature exceeds 250 ° C., precipitates are coarsened and the proof strength and creep resistance are lowered.
  • the heat treatment time is not particularly limited, but is preferably 1 to 30 hours. If the time is less than 1 hour, particularly when mass production is assumed, a non-uniform temperature distribution occurs in the coil or the sheet, and the material characteristics tend to become unstable. In consideration of productivity, the upper limit is 30 hours.
  • the manufacturing method of the aluminum alloy plate for connecting parts according to the present invention is as described above. However, in carrying out the present invention, other processes may be performed between or before and after the respective steps within a range that does not adversely affect the respective steps. These steps may be included. For example, after the artificial aging treatment step S5, a cutting step for cutting into a predetermined size or a processing step for processing into a predetermined shape (bending, punching, etc.) as shown in FIG. 1 may be included. In addition, as for conditions that are not clearly shown in the respective steps, it is sufficient to use conventionally known conditions, and it is needless to say that the conditions can be appropriately changed as long as the effects obtained by the processing in the respective steps are exhibited.
  • An aluminum alloy plate for connecting parts according to the present invention contains a predetermined amount of Si and Mg, and the balance is made of an aluminum alloy composed of Al and inevitable impurities, and has a conductivity, And the Cube orientation distribution density of the plate surface is not less than a predetermined value and the crystal grain size is not more than a predetermined value.
  • the aluminum alloy plate for connecting parts according to the present invention preferably has Fe and Zn of unavoidable impurities less than a predetermined value, and is selected from Cu, Mn, Cr, Zr, and Ti that are less than a predetermined value. More preferably, it contains seeds or more.
  • the Cube orientation distribution density on the plate surface of the aluminum alloy plate for connection parts according to the present invention is 20 or more.
  • the Cube orientation distribution density on the plate surface of the aluminum alloy plate for connection parts according to the present invention is 20 or more.
  • both creep resistance and bending workability required for connecting parts can be achieved.
  • the Cube orientation distribution density on the surface of the plate is less than 20, bending workability is deteriorated.
  • the Cube orientation distribution density is preferably 30 or more, and more preferably 50 or more, in order to ensure the effect of improving creep resistance and bending workability.
  • the Cube orientation distribution density is less than 20, which indicates that the crystal orientation of the plate surface is relatively random.
  • the Cube orientation distribution density is 20 or more, that is, when the Cube orientation is accumulated more than a certain amount, the proportion of small-angle grain boundaries having a small orientation difference between adjacent crystal grains increases. Reduce or eliminate grain boundary step during deformation.
  • the Cube orientation since a uniform slip deformation is possible compared to other orientations, formation of a shear band is suppressed.
  • the bending workability can be improved by setting the Cube orientation distribution density to 20 or more. Can improve (improve). If the Cube orientation distribution density is excessively increased, the manufacturing conditions become severe and the productivity is lowered. Therefore, the Cube orientation distribution density is preferably 100 or less.
  • the Cube orientation distribution density is set to 20 or more, even when compared with the same level of proof stress, the creep resistance required for the connecting parts can be improved.
  • the reason for this is not necessarily clear, it is known that the Cube orientation has a small Taylor factor and a small momentum of dislocation (Sai ⁇ ⁇ Ki et al .: Light Metal, 49 (1999), P. 583), which is presumed to be due to suppression of recovery during high temperature holding.
  • the aluminum alloy plate for connecting parts according to the present invention has an average crystal grain size in the rolling direction on the plate surface of 150 ⁇ m or less.
  • the average grain size in the rolling direction is 150 ⁇ m or less, the surface quality during bending can be improved.
  • the average crystal grain size in the rolling direction exceeds 150 ⁇ m, the possibility of rough skin and cracks on the surface during bending increases.
  • the average crystal grain size in the rolling direction is preferably 100 ⁇ m or less, and more preferably 50 ⁇ m or less, in order to ensure the effect of improving the surface quality during bending.
  • the average crystal grain size in the rolling direction is preferably 10 ⁇ m or more because manufacturing conditions become stricter and productivity is lowered when trying to make it excessively small.
  • the average particle size in the rolling direction can be measured by cutting a measurement piece from an aluminum alloy plate, polishing the plate surface, etching it with an electrolytic solution, and observing it at about 100 times with an optical microscope.
  • the average grain size in the rolling direction is achieved by controlling the hot rolling start temperature and rolling end temperature in the aluminum alloy sheet manufacturing process.
  • the method for producing an aluminum alloy plate for connecting parts includes a homogenization heat treatment step S2, a hot rolling step S3, a solution heat treatment step S4, and an artificial aging treatment step S5. .
  • a homogenization heat treatment step S2 a hot rolling step S3, a solution heat treatment step S4, and an artificial aging treatment step S5. .
  • steps different from those of the first embodiment will be described. Since others are the same as that of 1st Embodiment, description is abbreviate
  • the homogenized ingot is hot rolled.
  • the rolling start temperature at this time is set to 350 to 450 ° C.
  • a hot rolled plate (hot coil) having a desired thickness is obtained.
  • the aspect of cooling to a temperature range of 350 to 450 ° C. where the hot rolling is started may be directly cooled to this temperature range and the hot rolling may be started within this temperature range. (Hereinafter also referred to as two-stage soaking).
  • the temperature may be cooled to a temperature range of 350 ° C. or lower, and then reheated to a temperature range of 350 to 450 ° C. where hot rolling is started, and hot rolling may be started in this temperature range (hereinafter, Also called twice soaking).
  • the hot rolling start temperature exceeds 450 ° C, it causes rough skin during bending. Moreover, if the hot rolling start temperature is less than 350 ° C., the hot rolling itself becomes difficult.
  • the present invention is characterized in that the cold rolling process is not performed after hot rolling, and thus the structure control of the hot rolled sheet is very important.
  • the present inventors have found that recrystallized grains generated during hot rolling tend to be coarse and this structure is maintained even after solution heat treatment, which causes rough skin during bending.
  • the hot rolling start temperature 450 ° C. or less, recrystallization during hot rolling can be suppressed, and the crystal grain size after the subsequent solution heat treatment can be set to a predetermined value or less.
  • an Mg 2 Si compound is formed in the ingot, and this Mg 2 Si compound is a nucleation site of recrystallized grains during the solution heat treatment Therefore, the crystal grain size can be reduced.
  • the cooling rate to the hot rolling start temperature range after the homogenization heat treatment is not particularly specified, it is preferably in the range of 20 to 200 ° C./h.
  • the cooling rate is 20 ° C./h or less, the Mg 2 Si compound becomes coarse. Therefore, if it is attempted to re-solidify the Mg 2 Si compound in order to obtain a desired strength, a solution heat treatment is required for a long time, and productivity is increased. descend.
  • the cooling rate is too high at 200 ° C./h, the temperature distribution in the ingot becomes non-uniform, and there is a possibility that a new problem in which an abnormality such as deformation or warping due to heat shrinkage occurs.
  • Cooling means after homogenization heat treatment there are, for example, forced fan air cooling in the soaking furnace or outside the furnace, contact cooling, and cooling by mist or spray.
  • the hot rolling finish temperature is not specified. However, by lowering the hot rolling end temperature to 300 ° C. or less in particular, the accumulated strain during hot rolling can be increased and the recrystallization driving force in the subsequent solution heat treatment can be increased. The recrystallized grain size can be further refined while increasing the Cube orientation distribution density.
  • the holding time at the heat treatment temperature in the solution heat treatment step S4 is within 100 seconds (may be 0 seconds). This is because when the time exceeds 100 seconds, the effect is saturated and the productivity is lowered. Since others are the same as that of 1st Embodiment, description is abbreviate
  • the rate of temperature increase from 200 ° C. to the heat treatment temperature is preferably 5 ° C./s or more, and the rate of temperature decrease from the heat treatment temperature to 200 ° C. is 10 ° C./s or more. preferable.
  • Example 1 Example of the first embodiment
  • Aluminum alloys (alloys 1 to 17) having the compositions shown in Table 1 were melted, ingots were produced by semi-continuous casting, and face machining was performed. The ingot was subjected to homogenization heat treatment under the conditions shown in Table 2, and then subjected to hot rolling at a rolling rate of 99% continuously without cooling (hot rolling end temperature is Table 2). A rolled sheet was used. Thereafter, cold rolling was not performed (the test materials 20 and 21 were cold rolled), and solution heat treatment was performed under the conditions shown in Table 2. Then, after the solution heat treatment, a sample material (thickness 2 mm) was produced by performing an artificial aging treatment (not performed on the sample material 20) that is held at 200 ° C. for 2 hours.
  • Test test A test piece of JIS No. 5 was cut out from the specimen so that the tensile direction was parallel to the rolling direction. Using this test piece, a tensile test was performed in accordance with JIS Z 2241, and tensile strength, yield strength (0.2% yield strength), and elongation were measured. The crosshead speed was 5 mm / min, and the test was performed at a constant speed until the test piece broke.
  • Cube orientation distribution density was determined by measuring the surface of the prepared specimen using an X-ray diffractometer manufactured by Rigaku Corporation [model “Rigaku RAD-rX” (Ru-200B)]. ODF analysis was performed using an incomplete pole figure using the X-ray diffractometer. In detail, the incomplete pole figure of ⁇ 100 ⁇ plane and ⁇ 111 ⁇ plane is created by schluz reflection method, ODF analysis is performed by applying Bunge's iterative series expansion method (positivity method), and Cube orientation The distribution density was determined.
  • the conductivity was measured by an eddy current conductivity measuring device [model “Sigma Test D2.068”] manufactured by FOERSTER JAPAN Limited. In addition, the measurement of the conductivity was performed at any five locations on the surface of the test material with a space of 100 mm or more between each other.
  • the electrical conductivity in the present invention is obtained by averaging the measured electrical conductivities.
  • a test piece of JIS No. 3 (JIS Z 2204) was cut out from the specimen so that the longitudinal direction of the test piece coincided with the rolling direction.
  • the test piece was subjected to a bending test by the V-block method according to JIS Z 2248 (see FIG. 3), and the bending workability was evaluated.
  • the bending test was performed under the conditions of ⁇ (bending angle): 90 °, r (inner bending radius): 0 mm, and t (test material plate thickness): 2 mm.
  • residual stress ratio value 75% or more, it has the ability to withstand the phenomenon (creep) that is deformed by continuous stress at high temperature, that is, it has the creep resistance required for connecting parts. evaluated.
  • Table 1 or 2 shows the detailed components of the aluminum alloy, the production conditions of the test material, and the material characteristics (test results). In Tables 1 and 2, numerical values that do not satisfy the configuration of the present invention are underlined.
  • the specimen 10 (alloy 9) had a Si content that was less than the lower limit of the numerical range defined in the present invention, and the Mg content exceeded the upper limit of the numerical range defined in the present invention.
  • the proof stress did not exceed a predetermined value, and as a result, the evaluation was that the bending workability and creep resistance were not excellent.
  • the Si content exceeded the upper limit of the numerical range defined in the present invention, and the Mg content was less than the lower limit of the numerical range defined in the present invention.
  • the bending workability and creep resistance were not excellent.
  • test materials 12 to 18 (alloys 11 to 17) had a value greater than the value specified in the present invention, any one of Fe, Zn, Cu, Mn, Cr, Zr, and Ti had bending workability.
  • the evaluation was bad ( ⁇ ).
  • the Cube orientation distribution density was less than a predetermined value, resulting in poor bending workability (x). Furthermore, since the sample material 20 was subjected to batch furnace annealing (240 ° C. ⁇ 5 hours (temperature increase rate: 50 ° C./hour, temperature decrease rate: 50 ° C./hour)) as a solution heat treatment, the creep resistance was improved. The evaluation was not good.
  • the test material 22 was burned, and the subsequent manufacturing and testing could not be performed.
  • sample material 20 assumes the aluminum alloy plate described in Patent Document 2
  • sample material 21 assumes the aluminum alloy plate described in Patent Document 1.
  • Aluminum alloys (alloys 1 to 17) having the compositions shown in Table 1 were melted, ingots were produced by semi-continuous casting, and face machining was performed. This ingot was subjected to homogenization heat treatment under the conditions shown in Table 3, and then subjected to hot rolling at a rolling rate of 99% continuously without cooling (hot rolling end temperature is Table 3). A rolled sheet was used.
  • test material thickness 2 mm
  • solution heat treatment was performed under the conditions shown in Table 3.
  • a test material thickness 2 mm
  • hot rolling was performed by two-stage soaking, and for the test materials 5 to 18, 20, and 23, hot rolling was performed twice by soaking.
  • Table 1 or Table 3 shows detailed aluminum alloy components, production conditions of the test materials, and material characteristics (test results). In Tables 1 and 3, numerical values that do not satisfy the configuration of the present invention are underlined.
  • the test material 20 was burned, and the subsequent manufacturing and testing could not be performed.
  • the Cube orientation distribution density was less than a predetermined value, resulting in poor bending workability. Furthermore, since the sample material 24 was subjected to batch furnace annealing (240 ° C. ⁇ 5 hours (temperature increase rate: 50 ° C./hour, temperature decrease rate: 50 ° C./hour)) as a solution heat treatment, the creep resistance was improved. The evaluation was not good.
  • sample material 24 assumes the aluminum alloy plate described in Patent Document 2
  • sample material 25 assumes the aluminum alloy plate described in Patent Document 1.

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Abstract

The present invention addresses the problem of providing an aluminum alloy sheet for connecting components which exhibits excellent creep resistance and bendability while keeping excellent conductivity and a manufacturing process therefor. This aluminum alloy sheet is characterized by: consisting of an aluminum alloy that contains 0.3 to 1.5 mass% of Si and 0.3 to 1.0 mass% of Mg with the balance being Al and unavoidable impurities; exhibiting a conductivity of 45.0% IACS or higher; and exhibiting a Cube orientation density of 15 or more on the surface of the sheet as determined by orientation distribution function analysis.

Description

接続部品用アルミニウム合金板およびその製造方法Aluminum alloy plate for connecting parts and manufacturing method thereof
　本発明は、電気自動車を始めとする電気を動力源とした各種電動輸送機器等に搭載されている電気機器（電池群、インバータ、モータ等）間または電気機器内部の部品間を、電気的に接続する接続部品に用いる接続部品用アルミニウム合金板およびその製造方法に関するものである。 The present invention electrically connects between electric devices (batteries, inverters, motors, etc.) mounted on various electric transportation devices using electricity as a power source such as an electric vehicle or between components inside the electric device. The present invention relates to an aluminum alloy plate for connecting parts used for connecting parts to be connected and a method for manufacturing the same.
　電気自動車を始めとする電気を動力源とした各種電動輸送機器（ハイブリッド自動車、燃料電池自動車、電気機関車等）には、電池群、インバータ、モータ等の各種の電気機器が搭載されている。そして、これらの電気機器間または電気機器内部の部品間を電気的に接続するにあたり、バスバー（ｂｕｓ－ｂａｒ）と呼ばれる接続部品が使用されている。 Various electric devices such as a battery group, an inverter, and a motor are mounted on various electric transport devices (hybrid vehicle, fuel cell vehicle, electric locomotive, etc.) that use electricity as a power source including an electric vehicle. In order to electrically connect between these electric devices or between the components in the electric device, a connecting component called a bus-bar is used.
　この接続部品は、電気を通さなければならないため、当然、導電性に優れる必要がある。
　また、当該接続部品をボルト等の連結具により連結する場合、通電時の発熱により接続部品１の連結部１ａ（図１参照）の変形（クリープ変形）が生じることにより、連結具の締め付けトルクが低下して、連結具が緩んだり外れたりすることがないように、接続部品は高い耐クリープ性を備える必要がある。
　さらに、電気機器の省スペース化（小型化）の要望を満たすため、接続部品は、曲げ半径（Ｒ）が小さな湾曲部分を有する形状に設計される場合が多い。したがって、接続部品は、曲げ加工性にも優れる必要がある。 Since this connection component must conduct electricity, it is naturally necessary to have excellent conductivity.
Further, when the connecting part is connected by a connecting tool such as a bolt, deformation (creep deformation) of the connecting part 1a (see FIG. 1) of the connecting part 1 occurs due to heat generation when energized, so that the tightening torque of the connecting tool is increased. The connecting parts must have a high creep resistance so that they do not drop and the couplings come loose or come off.
Furthermore, in order to satisfy the demand for space saving (miniaturization) of electrical equipment, the connecting component is often designed in a shape having a curved portion with a small bending radius (R). Therefore, the connection component needs to be excellent in bending workability.
　これまで、上記のような条件を満たす接続部品について、銅を主体とした素材について検討されてきた。
　しかしながら、近年、自動車の燃費を低減するために、自動車の軽量化、ひいては、自動車に搭載される電気機器の軽量化が求められている。
　上記の事情を勘案し、銅よりも軽量であるアルミニウム合金からなる接続部品が提案されている。 Up to now, copper-based materials have been studied for connecting parts that satisfy the above conditions.
However, in recent years, in order to reduce the fuel consumption of automobiles, it has been required to reduce the weight of automobiles and, in turn, to reduce the weight of electrical devices mounted on automobiles.
In view of the above circumstances, connecting parts made of an aluminum alloy that is lighter than copper have been proposed.
　例えば、特許文献１には、成分組成を特定するとともに、導電率および調質の条件を特定した接続部品用のアルミニウム合金が開示されている。そして、特許文献１には、当該アルミニウム合金は、導電性に優れるとともに、耐クリープ性にも優れると記載されている。 For example, Patent Document 1 discloses an aluminum alloy for connection parts in which the component composition is specified and the conditions of conductivity and tempering are specified. Patent Document 1 describes that the aluminum alloy has excellent conductivity and excellent creep resistance.
　また、特許文献２には、成分組成が特定された鋳塊に、所定条件の均質化熱処理、熱間圧延、冷間圧延、最終焼鈍を施すアルミニウム合金板の製造方法が開示されている。そして、特許文献２には、当該製造方法で製造されたアルミニウム合金板は、プリント基板に要求される曲げ加工性を有すると記載されている。 Further, Patent Document 2 discloses a method for producing an aluminum alloy sheet in which a homogenized heat treatment, hot rolling, cold rolling, and final annealing under predetermined conditions are performed on an ingot with a specified component composition. And in patent document 2, it describes that the aluminum alloy plate manufactured with the said manufacturing method has the bending workability requested | required of a printed circuit board.
　さらに、特許文献３、４には、接続部品用ではなく自動車パネル用のアルミニウム合金板に関する技術ではあるが、Ａｌ－Ｍｇ－Ｓｉ系合金（ＪＩＳ６０００系のＡｌ合金）の曲げ加工性を向上させるために、集合組織を制御してＣｕｂｅ方位分布密度を所定値とする技術（特許文献３）や、全ての結晶粒間の粒界長さの合計に対し、方位差が２０°以下となる結晶粒間の粒界長さを特定する技術（特許文献４）が開示されている。 Further, Patent Documents 3 and 4 disclose a technique related to an aluminum alloy plate for an automobile panel, not for a connection part, in order to improve the bending workability of an Al—Mg—Si based alloy (JIS6000 based Al alloy). In addition, a technique in which the texture is controlled to set the Cube orientation distribution density to a predetermined value (Patent Document 3) or a crystal grain having an orientation difference of 20 ° or less with respect to the total grain boundary length between all crystal grains. A technique for specifying the intergranular length (Patent Document 4) is disclosed.
特許第３５５７１１６号公報Japanese Patent No. 3557116 特開２００９－２４２８１３号公報JP 2009-242813 A 特開２００５－２９８９２２号公報JP 2005-298922 A 特許第３７４９６８７号公報Japanese Patent No. 3749687
　しかしながら、特許文献１に開示された技術は、耐クリープ性の向上に着目した技術ではあるものの、曲げ加工性について全く考慮していない技術であることから（特許文献１の段落００１０等参照）、当然、接続部品に要求される曲げ加工性を満足できなかった。したがって、特許文献１に開示された技術を接続部品に適用した場合、成形加工時に表面に曲げ割れが発生してしまう可能性がある。 However, although the technique disclosed in Patent Document 1 is a technique that focuses on the improvement of creep resistance, it is a technique that does not consider bending workability at all (see paragraph 0010 of Patent Document 1). Naturally, the bending workability required for the connecting parts could not be satisfied. Therefore, when the technique disclosed in Patent Document 1 is applied to a connection part, a bending crack may occur on the surface during molding.
　また、特許文献２に開示された技術は、曲げ加工性の向上に着目した技術ではあるものの、耐クリープ性について全く考慮していない技術であることから（特許文献２の段落０００１等参照）、当然、接続部品に要求される耐クリープ性を満足できなかった。したがって、特許文献２に開示された技術を接続部品に適用した場合、通電時の発熱により接続部品１の連結部１ａ（図１参照）が変形することで、当該接続部品を連結するボルト等の連結具が緩んだり外れたりしてしまう可能性がある。 Further, although the technique disclosed in Patent Document 2 is a technique that focuses on the improvement of bending workability, it is a technique that does not consider creep resistance at all (see paragraph 0001 and the like in Patent Document 2). Of course, the creep resistance required for the connecting parts could not be satisfied. Therefore, when the technique disclosed in Patent Document 2 is applied to a connection component, a connecting portion 1a (see FIG. 1) of the connection component 1 is deformed by heat generated during energization, so that a bolt or the like for connecting the connection component can be obtained. There is a possibility that the connector will loosen or come off.
　なお、特許文献３、４に開示された技術は、特許文献２と同様、曲げ加工性については考慮しているが、耐クリープ性について全く考慮していない技術であるとともに、接続部品用ではなく自動車パネル用の技術である。したがって、特許文献３、４に開示された技術は、接続部品に要求される耐クリープ性を満足できるものではない。さらに、板厚１ｍｍ程度の自動車パネルに要求される曲げ加工性を有するとしても、接続部品は通常、板厚２ｍｍ程度であるため、接続部品に要求されるような高い曲げ加工性を有するとは考え難い。 Note that the techniques disclosed in Patent Documents 3 and 4 consider bending workability as well as Patent Document 2, but do not consider creep resistance at all, and are not for connecting parts. It is a technology for automobile panels. Therefore, the techniques disclosed in Patent Documents 3 and 4 do not satisfy the creep resistance required for connecting parts. Furthermore, even if it has the bending workability required for an automobile panel having a plate thickness of about 1 mm, the connecting part usually has a plate thickness of about 2 mm, so that it has a high bending workability as required for the connecting part. Hard to think.
　前記特許文献１～４の記載からわかるように、アルミニウム合金板について、接続部品として必須の特性である導電性を保持しつつ、接続部品に要求される耐クリープ性と曲げ加工性とを両立させた技術は存在しないと思われる。
　なお、この実情は、技術常識（金属から構成される板材の耐クリープ性を向上させるには強度を向上させる必要があるが、強度を向上させると板材の曲げ加工性が低下してしまう、つまり、耐クリープ性と曲げ加工性とはトレードオフの関係にある）に合致するものであり、当然のことであると考えられてきた。 As can be seen from the descriptions in Patent Documents 1 to 4, the aluminum alloy plate has both the creep resistance and the bending workability required for the connecting part while maintaining the conductivity that is an essential characteristic for the connecting part. No technology seems to exist.
In addition, this situation is technical common sense (in order to improve the creep resistance of a plate made of metal, it is necessary to improve the strength, but if the strength is improved, the bending workability of the plate will be reduced, that is, The creep resistance and the bending workability are in a trade-off relationship) and have been considered as a matter of course.
　そこで、本発明は、導電性を保持しつつ、耐クリープ性および曲げ加工性にも優れる接続部品用アルミニウム合金板およびその製造方法を提供することを課題とする。 Therefore, an object of the present invention is to provide an aluminum alloy plate for connection parts that is excellent in creep resistance and bending workability while maintaining conductivity, and a method for manufacturing the same.
　前記課題を解決するため、本発明の発明者らは、接続部品用アルミニウム合金板の板表面におけるＣｕｂｅ方位分布密度や、成分組成等が、耐クリープ性と曲げ加工性とに大きな影響を与えることを見出し、本発明を創出した。 In order to solve the above-mentioned problems, the inventors of the present invention show that the Cube orientation distribution density and the component composition on the surface of the aluminum alloy plate for connecting parts have a great influence on the creep resistance and bending workability. And found the present invention.
　すなわち、本発明に係る接続部品用アルミニウム合金板は、Ｓｉ：０．３～１．５質量％、Ｍｇ：０．３～１．０質量％を含有し、残部がＡｌおよび不可避的不純物からなるアルミニウム合金で構成され、導電率が４５．０％ＩＡＣＳ以上であり、結晶方位分布関数解析による板表面のＣｕｂｅ方位分布密度が１５以上である。 That is, the aluminum alloy plate for connecting parts according to the present invention contains Si: 0.3 to 1.5 mass%, Mg: 0.3 to 1.0 mass%, and the balance is made of Al and inevitable impurities. It is made of an aluminum alloy, has an electric conductivity of 45.0% IACS or more, and a Cube orientation distribution density on the plate surface by a crystal orientation distribution function analysis of 15 or more.
　この接続部品用アルミニウム合金板によれば、板表面のＣｕｂｅ方位分布密度を所定以上に特定していることから、耐クリープ性を向上させるとともに、曲げ加工性を向上させることができる。つまり、この接続部品用アルミニウム合金板によれば、接続部品に要求される耐クリープ性と曲げ加工性とを両立させることができる。
　また、この接続部品用アルミニウム合金板によれば、ＳｉおよびＭｇの含有量を所定範囲に特定していることから、耐クリープ性の向上という効果を確実なものとすることができる。
　さらに、この接続部品用アルミニウム合金板によれば、導電率を４５．０％ＩＡＣＳ以上に特定していることから、接続部品に要求される導電率を確保することができる。 According to the aluminum alloy plate for connecting parts, since the Cube orientation distribution density on the surface of the plate is specified more than a predetermined value, the creep resistance can be improved and the bending workability can be improved. That is, according to the aluminum alloy plate for connecting parts, both creep resistance and bending workability required for the connecting parts can be achieved.
Moreover, according to this aluminum alloy plate for connection parts, since the content of Si and Mg is specified within a predetermined range, the effect of improving creep resistance can be ensured.
Furthermore, according to this aluminum alloy plate for connection parts, since the electrical conductivity is specified to be 45.0% IACS or more, the electrical conductivity required for the connection parts can be ensured.
　また、本発明に係る接続部品用アルミニウム合金板は、前記不可避的不純物のうち、Ｆｅ：０．５質量％未満、Ｚｎ：０．５質量％未満であることが好ましい。 Moreover, the aluminum alloy plate for connection parts according to the present invention preferably includes Fe: less than 0.5 mass% and Zn: less than 0.5 mass% among the inevitable impurities.
　この接続部品用アルミニウム合金板によれば、不可避的不純物のうち、Ｆｅ、Ｚｎの含有量を所定値未満に特定していることから、曲げ加工性の向上という効果を確実なものとすることができる。 According to this aluminum alloy plate for connecting parts, the content of Fe and Zn among inevitable impurities is specified to be less than a predetermined value, so that the effect of improving the bending workability can be ensured. it can.
　また、本発明に係る接続部品用アルミニウム合金板は、前記アルミニウム合金が、Ｃｕ：１．０質量％未満、Ｍｎ：１．０質量％未満、Ｃｒ：０．５質量％未満、Ｚｒ：０．３質量％未満、Ｔｉ：０．１質量％未満、から選択される１種以上をさらに含有することが好ましい。 In the aluminum alloy plate for connecting parts according to the present invention, the aluminum alloy contains Cu: less than 1.0% by mass, Mn: less than 1.0% by mass, Cr: less than 0.5% by mass, Zr: 0.0. It is preferable to further contain one or more selected from less than 3% by mass and Ti: less than 0.1% by mass.
　この接続部品用アルミニウム合金板によれば、所定値未満のＣｕ、Ｍｎ、Ｃｒ、Ｚｒ、Ｔｉから選択される１種以上をさらに含有することから、曲げ加工性の向上という効果を確保しつつ、耐クリープ性の向上という効果をさらに確実なものとすることができる。 According to this aluminum alloy plate for connecting parts, since it further contains one or more selected from Cu, Mn, Cr, Zr, Ti less than a predetermined value, while ensuring the effect of improving the bending workability, The effect of improving the creep resistance can be further ensured.
　本発明に係る接続部品用アルミニウム合金板の製造方法は、前記アルミニウム合金からなる鋳塊に５００～５７０℃、１～２４時間の均質化熱処理を施す均質化熱処理工程と、前記均質化熱処理を施した鋳塊に熱間圧延を施して熱間圧延板を製造する熱間圧延工程と、前記熱間圧延板に冷間圧延を施さずに、５００～５７０℃、６０秒以下保持する溶体化熱処理を施す溶体化熱処理工程と、前記溶体化熱処理を施した熱間圧延板に人工時効処理を施す人工時効処理工程と、を含む。 The method for producing an aluminum alloy plate for connecting parts according to the present invention comprises a homogenization heat treatment step of subjecting an ingot made of the aluminum alloy to a homogenization heat treatment at 500 to 570 ° C. for 1 to 24 hours, and the homogenization heat treatment. A hot rolling process for producing a hot rolled sheet by subjecting the ingot to hot rolling, and a solution heat treatment for holding the hot rolled sheet at 500 to 570 ° C. for 60 seconds or less without subjecting the hot rolled sheet to cold rolling. And a solution heat treatment step of applying an artificial aging treatment to the hot-rolled sheet subjected to the solution heat treatment.
　この接続部品用アルミニウム合金板の製造方法によれば、使用するアルミニウム合金の成分組成を特定し、均質化熱処理および溶体化熱処理の条件を特定するとともに、冷間圧延を施さないことにより、当該製造方法により製造される接続部品用アルミニウム合金板の導電率、板表面のＣｕｂｅ方位分布密度および耐力を所定値以上とすることができる。 According to this method for manufacturing an aluminum alloy sheet for connecting parts, the component composition of the aluminum alloy to be used is specified, the conditions for the homogenization heat treatment and the solution heat treatment are specified, and the cold rolling is not performed. The electrical conductivity, the Cube orientation distribution density on the surface of the plate, and the proof stress of the aluminum alloy plate for connection parts manufactured by the method can be set to a predetermined value or more.
　前記結晶方位分布関数解析による板表面のＣｕｂｅ方位分布密度が２０以上、板表面における圧延方向の平均結晶粒径が１５０μｍ以下であることが好ましい。
　結晶粒径を微細化することで、曲げ表面品質を向上させることができる。 It is preferable that the Cube orientation distribution density on the plate surface by the crystal orientation distribution function analysis is 20 or more, and the average crystal grain size in the rolling direction on the plate surface is 150 μm or less.
Bending surface quality can be improved by reducing the crystal grain size.
　本発明に係る接続部品用アルミニウム合金板の製造方法は、前記アルミニウム合金からなる鋳塊に、５００～５７０℃、１～２４時間の均質化熱処理を施す均質加熱処理工程と、前記均質化熱処理を施した鋳塊に圧延開始温度を３５０～４５０℃とした複数のパスからなる圧延を施して熱間圧延板を製造する熱間圧延工程と、前記熱間圧延板に冷間圧延を施さずに、５００～５７０℃、１００秒以下保持する溶体化熱処理を施す溶体化熱処理工程と、前記溶体化熱処理を施した熱間圧延板に人工時効処理を施す人工時効処理工程と、を含む。 The method for producing an aluminum alloy plate for connecting parts according to the present invention comprises a homogeneous heat treatment step of subjecting an ingot made of the aluminum alloy to a homogenization heat treatment at 500 to 570 ° C. for 1 to 24 hours, and the homogenization heat treatment. A hot rolling step of producing a hot-rolled sheet by rolling a plurality of passes at a rolling start temperature of 350 to 450 ° C. on the ingot, and without subjecting the hot-rolled sheet to cold rolling , A solution heat treatment step for performing a solution heat treatment held at 500 to 570 ° C. for 100 seconds or less, and an artificial aging treatment step for subjecting the hot-rolled sheet subjected to the solution heat treatment to an artificial aging treatment.
　この接続部品用アルミニウム合金板の製造方法によれば、使用するアルミニウム合金の成分組成を特定し、均質化熱処理、熱間圧延および溶体化熱処理の条件を特定するとともに、冷間圧延を施さないことにより、当該製造方法により製造される接続部品用アルミニウム合金板の導電率、板表面のＣｕｂｅ方位分布密度および耐力を所定値以上、結晶粒径を所定値以下とすることができる。 According to this method of manufacturing an aluminum alloy plate for connecting parts, the component composition of the aluminum alloy to be used is specified, the conditions for the homogenization heat treatment, hot rolling and solution heat treatment are specified, and cold rolling is not performed. Thus, the electrical conductivity, the Cube orientation distribution density and the proof stress of the aluminum alloy plate for connecting parts manufactured by the manufacturing method can be set to a predetermined value or more and the crystal grain size can be set to a predetermined value or less.
　本発明に係る接続部品用アルミニウム合金板によれば、導電率、板表面のＣｕｂｅ方位分布密度を所定値以上と特定するとともに、ＳｉおよびＭｇの含有量を所定範囲に特定していることから、導電性を保持しつつ、耐クリープ性および曲げ加工性にも優れるので、接続部品として好適に使用することができる。 According to the aluminum alloy plate for connecting parts according to the present invention, the conductivity, the Cube orientation distribution density of the plate surface is specified as a predetermined value or more, and the contents of Si and Mg are specified in a predetermined range. Since it retains conductivity and is excellent in creep resistance and bending workability, it can be suitably used as a connection part.
　また、本発明に係る接続部品用アルミニウム合金板の製造方法によれば、使用するアルミニウム合金の組成を特定し、均質化熱処理および溶体化熱処理の条件を特定するとともに、冷間圧延を施さないことにより、導電性を保持しつつ、耐クリープ性および曲げ加工性にも優れる接続部品用アルミニウム合金板を製造することができる。 Moreover, according to the manufacturing method of the aluminum alloy plate for connecting parts according to the present invention, the composition of the aluminum alloy to be used is specified, the conditions for the homogenization heat treatment and the solution heat treatment are specified, and cold rolling is not performed. As a result, it is possible to produce an aluminum alloy plate for connecting parts that is excellent in creep resistance and bending workability while maintaining conductivity.
本発明の実施形態に係る接続部品（バスバー）の斜視図である。It is a perspective view of the connection component (bus bar) concerning the embodiment of the present invention. 本発明に係る接続部品用アルミニウム合金板の製造方法のフローチャートである。It is a flowchart of the manufacturing method of the aluminum alloy plate for connection components which concerns on this invention. 本発明の実施例における曲げ試験の方法を説明する模式図である。It is a schematic diagram explaining the method of the bending test in the Example of this invention.
　第１実施形態 First embodiment
　以下、本発明に係る接続部品用アルミニウム合金板およびその製造方法を実施するための形態について、詳細に説明する。 Hereinafter, an embodiment for carrying out an aluminum alloy plate for connecting parts and a manufacturing method thereof according to the present invention will be described in detail.
［接続部品用アルミニウム合金板］
　本発明に係る接続部品用アルミニウム合金板（以下、適宜、アルミニウム合金板という）は、所定量のＳｉおよびＭｇを含有し、残部がＡｌおよび不可避的不純物からなるアルミニウム合金で構成され、導電率、および板表面のＣｕｂｅ方位分布密度が所定値以上であることを特徴とする。
　また、本発明に係る接続部品用アルミニウム合金板は、不可避的不純物のうちＦｅ、Ｚｎが所定値未満であることが好ましく、所定値未満のＣｕ、Ｍｎ、Ｃｒ、Ｚｒ、Ｔｉから選択される１種以上を含有することがさらに好ましい。
　以下、本発明に係る接続部品用アルミニウム合金板の各合金成分、導電率、および板表面のＣｕｂｅ方位分布密度について数値限定した理由を説明する。 [Aluminum alloy plate for connecting parts]
An aluminum alloy plate for connecting parts according to the present invention (hereinafter, appropriately referred to as an aluminum alloy plate) contains a predetermined amount of Si and Mg, and the balance is made of an aluminum alloy composed of Al and inevitable impurities, and has a conductivity, And the Cube orientation distribution density on the plate surface is a predetermined value or more.
Further, the aluminum alloy plate for connecting parts according to the present invention preferably has Fe and Zn of unavoidable impurities less than a predetermined value, and is selected from Cu, Mn, Cr, Zr, and Ti that are less than a predetermined value. More preferably, it contains seeds or more.
Hereinafter, the reason why the alloy components, the electrical conductivity, and the Cube orientation distribution density on the surface of the aluminum alloy plate for connecting parts according to the present invention are numerically limited will be described.
（Ｓｉ：０．３～１．５質量％）
　Ｓｉは、Ｍｇとともに溶体化熱処理後の人工時効処理時に時効析出物を形成する。Ｓｉが高温環境下での転位の移動を阻害することで、耐クリープ性を向上させるため、Ｓｉは、本発明に係る接続部品用アルミニウム合金板に必須の元素である。
　Ｓｉの含有量が０．３質量％未満では、所望の耐クリープ性を得られない。一方、Ｓｉの含有量が１．５質量％を超えると粗大な晶出物、析出物が形成されて、特に曲げ加工性を劣化させる。
　したがって、Ｓｉの含有量は０．３～１．５質量％である。
　なお、曲げ加工性と耐クリープ性の向上という効果をより確実なものとするため、Ｓｉの含有量は０．４～１．５質量％であることが好ましく、０．５～１．３質量％であることがさらに好ましい。 (Si: 0.3-1.5% by mass)
Si forms aging precipitates together with Mg during the artificial aging treatment after solution heat treatment. Since Si inhibits the movement of dislocations in a high temperature environment and improves creep resistance, Si is an essential element for the aluminum alloy plate for connecting parts according to the present invention.
If the Si content is less than 0.3% by mass, desired creep resistance cannot be obtained. On the other hand, when the Si content exceeds 1.5% by mass, coarse crystallized substances and precipitates are formed, and particularly bending workability is deteriorated.
Therefore, the Si content is 0.3 to 1.5% by mass.
In order to ensure the effect of improving the bending workability and creep resistance, the Si content is preferably 0.4 to 1.5% by mass, preferably 0.5 to 1.3% by mass. % Is more preferable.
（Ｍｇ：０．３～１．０質量％）
　Ｍｇは、Ｓｉとともに溶体化熱処理後の人工時効処理時に時効析出物を形成する。Ｍｇが高温環境下での転位の移動を阻害することで、耐クリープ性を向上させるため、Ｍｇは、本発明に係る接続部品用アルミニウム合金板に必須の元素である。
　Ｍｇの含有量が０．３質量％未満では、所望の耐クリープ性を得られない。一方、Ｍｇの含有量が１．０質量％を超えると粗大な晶出物、析出物が形成されて、特に曲げ加工性を劣化させる。
　したがって、Ｍｇの含有量は０．３～１．０質量％である。
　なお、曲げ加工性と耐クリープ性の向上という効果をより確実なものとするため、Ｍｇの含有量は０．５～０．８質量％であることが好ましい。 (Mg: 0.3-1.0% by mass)
Mg forms an aging precipitate during the artificial aging treatment after solution heat treatment with Si. Since Mg inhibits the movement of dislocations under a high temperature environment and improves creep resistance, Mg is an essential element for the aluminum alloy plate for connecting parts according to the present invention.
If the Mg content is less than 0.3% by mass, desired creep resistance cannot be obtained. On the other hand, when the Mg content exceeds 1.0% by mass, coarse crystallized substances and precipitates are formed, and bending workability is particularly deteriorated.
Therefore, the Mg content is 0.3 to 1.0 mass%.
The Mg content is preferably 0.5 to 0.8% by mass in order to ensure the effect of improving bending workability and creep resistance.
（不可避的不純物）
　不可避的不純物として、Ｆｅ、Ｚｎ等が本発明の効果を妨げない範囲で含有されていてもよい。詳細には、ＦｅとＺｎは、それぞれ、０．５０質量％未満であること（０．５０質量％未満に制限されていること）が好ましい。Ｆｅの含有量またはＺｎの含有量が０．５０質量％以上となると曲げ加工性または耐蝕性が低下してしまうからである。
　なお、Ｆｅ、Ｚｎは、スクラップや再生地金（例えば、ブレージングシート(brazing sheet)等のクラッド材用のアルミニウム合金材の屑等）にある程度含有していることから、製造（溶解）時にスクラップや再生地金を、アルミニウム合金板におけるＦｅ、Ｚｎの含有量が前記範囲未満となる程度で配合することができ、原料コストを低減することができる。
　また、不可避的不純物として、本発明の効果を妨げない程度に、Ｆｅ、Ｚｎ以外の元素が含まれていてもよい。 (Inevitable impurities)
As an unavoidable impurity, Fe, Zn, or the like may be contained within a range that does not hinder the effects of the present invention. Specifically, Fe and Zn are each preferably less than 0.50% by mass (restricted to less than 0.50% by mass). This is because if the Fe content or Zn content is 0.50% by mass or more, the bending workability or the corrosion resistance is lowered.
Fe and Zn are contained to some extent in scrap and recycled metal (for example, scraps of aluminum alloy materials for clad materials such as brazing sheets). The recycled metal can be blended so that the content of Fe and Zn in the aluminum alloy plate is less than the above range, and the raw material cost can be reduced.
Moreover, elements other than Fe and Zn may be contained as unavoidable impurities to the extent that the effects of the present invention are not hindered.
（Ｃｕ：１．００質量％未満）
　Ｃｕは、溶体化熱処理後の人工時効処理における時効析出物形成を促進する。Ｃｕが高温環境下での転位の移動を阻害することで、耐クリープ性を向上させる。
　当該効果を得るためには、Ｃｕを０．０５質量％以上含有させるのが好ましい。
　一方、Ｃｕの含有量が１．００質量％以上であると耐応力腐食割れ性や溶接性、曲げ加工性を著しく劣化させる。
　したがって、Ｃｕをアルミニウム合金板に含有させる場合、Ｃｕの含有量は、１．００質量％未満である。 (Cu: less than 1.00% by mass)
Cu accelerates aging precipitate formation in the artificial aging treatment after the solution heat treatment. By inhibiting the movement of dislocations in a high temperature environment, Cu improves creep resistance.
In order to acquire the said effect, it is preferable to contain Cu 0.05 mass% or more.
On the other hand, if the Cu content is 1.00% by mass or more, the stress corrosion cracking resistance, weldability, and bending workability are remarkably deteriorated.
Therefore, when Cu is contained in the aluminum alloy plate, the Cu content is less than 1.00% by mass.
（Ｍｎ：１．００質量％未満）
　Ｍｎは、均質化熱処理時に分散粒子（分散相）を生成し、これらの分散粒子は再結晶後の粒界移動を妨げる。よって、Ｍｎは、結晶粒を微細化させる効果がある元素である。なお、本発明に係る接続部品用アルミニウム合金板の曲げ加工性は、アルミニウム合金組織の結晶粒が微細なほど向上する。
　当該効果を得るためには、Ｍｎを０．０１質量％以上含有させるのが好ましい。
　一方、Ｍｎの含有量が１．００質量％以上であると溶解、鋳造時に粗大なＡｌ－Ｆｅ－Ｓｉ－Ｍｎ系の晶出物を生成しやすく、かえって曲げ加工性を低下させる原因となる。
　したがって、Ｍｎをアルミニウム合金板に含有させる場合、Ｍｎの含有量は、１．００質量％未満である。 (Mn: less than 1.00% by mass)
Mn generates dispersed particles (dispersed phase) during the homogenization heat treatment, and these dispersed particles hinder grain boundary movement after recrystallization. Therefore, Mn is an element that has an effect of refining crystal grains. In addition, the bending workability of the aluminum alloy plate for connection parts according to the present invention improves as the crystal grains of the aluminum alloy structure become finer.
In order to acquire the said effect, it is preferable to contain 0.01 mass% or more of Mn.
On the other hand, if the Mn content is 1.00% by mass or more, a coarse Al—Fe—Si—Mn-based crystallized product is likely to be formed during melting and casting, which causes a decrease in bending workability.
Therefore, when Mn is contained in the aluminum alloy plate, the Mn content is less than 1.00% by mass.
（Ｃｒ：０．５０質量％未満）
　Ｃｒは、Ｍｎと同様に均質化熱処理時に分散粒子（分散相）を生成し、これらの分散粒子は再結晶後の粒界移動を妨げる。よって、Ｃｒは、結晶粒を微細化させる効果がある元素である。
　当該効果を得るためには、Ｃｒを０．０１質量％以上含有させるのが好ましい。
　一方、Ｃｒの含有量が０．５０質量％以上であると溶解、鋳造時に粗大な金属間化合物を生成しやすく、かえって曲げ加工性を劣化させる。
　したがって、Ｃｒをアルミニウム合金板に含有させる場合、Ｃｒの含有量は、０．５０質量％未満である。 (Cr: less than 0.50% by mass)
Cr, like Mn, produces dispersed particles (dispersed phase) during the homogenization heat treatment, and these dispersed particles hinder grain boundary movement after recrystallization. Therefore, Cr is an element that has an effect of refining crystal grains.
In order to acquire the said effect, it is preferable to contain 0.01 mass% or more of Cr.
On the other hand, if the Cr content is 0.50% by mass or more, a coarse intermetallic compound is likely to be produced during melting and casting, and the bending workability is deteriorated.
Therefore, when Cr is contained in the aluminum alloy plate, the Cr content is less than 0.50% by mass.
（Ｚｒ：０．３０質量％未満）
　Ｚｒは、Ｍｎと同様に均質化熱処理時に分散粒子（分散相）を生成し、これらの分散粒子は再結晶後の粒界移動を妨げる。よって、Ｚｒは、結晶粒を微細化させる効果がある元素である。
　当該効果を得るためには、Ｚｒを０．０１質量％以上含有させるのが好ましい。
　一方、Ｚｒの含有量が０．３０質量％以上であると溶解、鋳造時に粗大な金属間化合物を生成しやすく、かえって曲げ加工性を劣化させる。
　したがって、Ｚｒをアルミニウム合金板に含有させる場合、Ｚｒの含有量は、０．３０質量％未満である。 (Zr: less than 0.30% by mass)
Zr, like Mn, generates dispersed particles (dispersed phase) during the homogenization heat treatment, and these dispersed particles hinder grain boundary movement after recrystallization. Therefore, Zr is an element that has an effect of refining crystal grains.
In order to acquire the said effect, it is preferable to contain Zr 0.01 mass% or more.
On the other hand, when the Zr content is 0.30 mass% or more, a coarse intermetallic compound is likely to be produced during melting and casting, and bending workability is deteriorated.
Therefore, when Zr is contained in the aluminum alloy plate, the content of Zr is less than 0.30% by mass.
（Ｔｉ：０．１０質量％未満）
　Ｔｉは、微量含有させることで、鋳塊の結晶粒を微細化し、曲げ加工性を向上させる効果がある元素である。
　当該効果を得るためには、Ｔｉを０．０１質量％以上含有させるのが好ましい。
　一方、Ｔｉの含有量が０．１０質量％以上であると粗大な化合物を形成して曲げ加工性を劣化させる。
　したがって、Ｔｉをアルミニウム合金板に含有させる場合、Ｔｉの含有量は、０．１０質量％未満である。 (Ti: less than 0.10% by mass)
Ti is an element having the effect of making the crystal grains of the ingot finer and improving the bending workability by containing a small amount of Ti.
In order to acquire the said effect, it is preferable to contain Ti 0.01 mass% or more.
On the other hand, if the Ti content is 0.10% by mass or more, a coarse compound is formed and bending workability is deteriorated.
Therefore, when Ti is contained in the aluminum alloy plate, the Ti content is less than 0.10% by mass.
（導電率：４５．０％ＩＡＣＳ以上）
　本発明に係る接続部品用アルミニウム合金板の導電率は、４５．０％ＩＡＣＳ以上とする。
　導電率が４５．０％ＩＡＣＳ以上であると、接続機器としての導電性能を確保することができる。一方、電気抵抗が高い、すなわち導電率が４５．０％ＩＡＣＳ未満であると、所望の電流を流すために接続部品の断面積を増加させる必要が生じ、部品重量の増加に繋がってしまう。
　なお、導電率については、高ければ高いほどよく、好ましくは４７．０％ＩＡＣＳ以上、さらに好ましくは５０．０％ＩＡＣＳ以上である。 (Conductivity: 45.0% IACS or higher)
The electrical conductivity of the aluminum alloy plate for connecting parts according to the present invention is 45.0% IACS or more.
When the electrical conductivity is 45.0% IACS or more, electrical conductivity as a connected device can be ensured. On the other hand, if the electrical resistance is high, that is, the conductivity is less than 45.0% IACS, it is necessary to increase the cross-sectional area of the connecting component in order to flow a desired current, leading to an increase in the component weight.
The conductivity is preferably as high as possible, preferably 47.0% IACS or more, and more preferably 50.0% IACS or more.
　なお、導電率の調整は、アルミニウム合金板におけるＳｉの含有量、Ｍｇの含有量、アルミニウム合金板の製造工程における均質化熱処理条件、溶体化熱処理条件、人工時効処理条件を制御することによって達成される。
　なお、導電率を高くしすぎると、すなわち過度な固溶量減少および析出物粗大化が生じることにより耐クリープ性が低下する傾向にあるため、導電率は６０％ＩＡＣＳ以下であるのが好ましい。 The adjustment of conductivity is achieved by controlling the Si content, Mg content, homogenization heat treatment conditions, solution heat treatment conditions, and artificial aging conditions in the aluminum alloy sheet manufacturing process. The
If the conductivity is too high, that is, the creep resistance tends to decrease due to excessive decrease in the amount of solid solution and coarsening of precipitates, the conductivity is preferably 60% IACS or less.
（Ｃｕｂｅ方位分布密度：１５以上）
　本発明に係る接続部品用アルミニウム合金板の板表面におけるＣｕｂｅ方位分布密度は１５以上とする。
　板表面におけるＣｕｂｅ方位分布密度が１５以上であることにより、接続部品に要求される耐クリープ性と曲げ加工性とを両立させることができる。一方、板表面におけるＣｕｂｅ方位分布密度が１５未満であると、曲げ加工性が低下してしまう。
　なお、耐クリープ性および曲げ加工性の向上という効果をより確実なものとするため、Ｃｕｂｅ方位分布密度は、好ましくは２０以上、さらに好ましくは３０以上である。 (Cube orientation distribution density: 15 or more)
The Cube orientation distribution density on the surface of the aluminum alloy plate for connection parts according to the present invention is 15 or more.
When the Cube orientation distribution density on the plate surface is 15 or more, both creep resistance and bending workability required for the connecting parts can be achieved. On the other hand, if the Cube orientation distribution density on the surface of the plate is less than 15, bending workability is deteriorated.
The Cube orientation distribution density is preferably 20 or more, more preferably 30 or more, in order to ensure the effect of improving creep resistance and bending workability.
　なお、一般的な製造方法によれば、Ｃｕｂｅ方位分布密度は１５未満となるが、これは板表面の結晶方位が比較的ランダムであることを示す。
　一方、本発明が規定するように、Ｃｕｂｅ方位分布密度を１５以上とすると、つまり、Ｃｕｂｅ方位が一定量以上集積すると、隣り合う結晶粒との方位差の小さい小角粒界の割合が大きくなり、変形時の粒界段差を小さく、あるいは生じなくさせる。
　また、Ｃｕｂｅ方位においては、他の方位と比較して均一なすべり変形が可能になることからせん断帯の形成が抑制される。
　この結果、曲げ加工の際に割れの起点あるいは伝播経路となる粒界段差や結晶粒内でのせん断帯形成が抑制されるため、Ｃｕｂｅ方位分布密度を１５以上とすることにより、曲げ加工性を改善（向上）できる。
　なお、過度にＣｕｂｅ方位分布密度を高めようとすると、製造条件が厳しくなり生産性の低下を招くため、Ｃｕｂｅ方位分布密度は１００以下であるのが好ましい。 According to a general manufacturing method, the Cube orientation distribution density is less than 15, which indicates that the crystal orientation of the plate surface is relatively random.
On the other hand, as specified by the present invention, when the Cube orientation distribution density is 15 or more, that is, when the Cube orientation is accumulated more than a certain amount, the ratio of small-angle grain boundaries having a small orientation difference between adjacent crystal grains increases. Reduce or eliminate grain boundary step during deformation.
In addition, in the Cube orientation, since a uniform slip deformation is possible compared to other orientations, formation of a shear band is suppressed.
As a result, since the formation of a shear boundary in the grain boundary step and the crystal grain that becomes the starting point or propagation path of the crack in bending is suppressed, the bending workability is improved by setting the Cube orientation distribution density to 15 or more. Can improve (improve).
If the Cube orientation distribution density is excessively increased, the manufacturing conditions become severe and the productivity is lowered. Therefore, the Cube orientation distribution density is preferably 100 or less.
　本発明では、Ｃｕｂｅ方位分布密度を規定するに際し、結晶集合組織の測定精度がより正確な、結晶方位分布関数解析（以下、適宜、ＯＤＦ解析という）によるＣｕｂｅ方位分布密度で規定する。 In the present invention, when defining the Cube orientation distribution density, the Cube orientation distribution density is defined by the Cube orientation distribution density by crystal orientation distribution function analysis (hereinafter, referred to as ODF analysis as appropriate) with more accurate crystal texture measurement accuracy.
　ＯＤＦ解析によるＣｕｂｅ方位分布密度は、Ｃｕｂｅ方位をランダム方位（標準サンプルの無配向性のＡｌ粉末試料）からの比（無次元）で表すため、広い範囲を定量的に表現できる。これに対し、積分強度による測定では、面内（１００面）の回転方位を分離できないため、純粋なＣｕｂｅ方位だけを抽出できない。 The Cube orientation distribution density by ODF analysis can express a wide range quantitatively because the Cube orientation is represented by a ratio (dimensionalless) from a random orientation (non-oriented Al powder sample of a standard sample). On the other hand, in the measurement based on the integrated intensity, since the in-plane (100 plane) rotational orientation cannot be separated, only a pure Cube orientation cannot be extracted.
　このアルミニウム合金板の板表面におけるＯＤＦ解析によるＣｕｂｅ方位分布密度の測定は、例えば、株式会社リガク(Rigaku Corporation)製のＸ線回折装置［型式「リガクＲＡＤ－ｒＸ」（Ｒｕ－２００Ｂ）］を用い、板表面を計測することで行なう。上記Ｘ線回折装置は不完全極点図によるＯＤＦ解析が可能である。即ち、ｓｃｈｌｕｚの反射法により、｛１００｝面、｛１１１｝面の不完全極点図を作成し、Ｂｕｎｇｅの反復級数展開法（ｐｏｓｉｔｉｖｉｔｙ法）を適用してＯＤＦ解析を実施し、Ｃｕｂｅ方位分布密度を求めることができる。 Cube orientation distribution density on the surface of the aluminum alloy plate by ODF analysis is measured using, for example, an X-ray diffractometer [model “Rigaku RAD-rX” (Ru-200B)] manufactured by Rigaku Corporation. This is done by measuring the plate surface. The X-ray diffractometer can perform ODF analysis with an incomplete pole figure. That is, incomplete pole figures of {100} plane and {111} plane are created by schluz reflection method, ODF analysis is performed by applying Bunge's iterative series expansion method (positivity method), and Cube orientation distribution density Can be requested.
　なお、アルミニウム合金板に曲げ加工を施す際における曲げ方向とＣｕｂｅ方位（配向方向）との関係について、板のＣｕｂｅ方位が板の曲げ方向と平行になるように（板の曲げ加工方向を素材板の圧延方向と平行あるいは直角にして）曲げ加工した場合には、変形中のＣｕｂｅ方位が安定となり、良好な曲げ加工性が得られる。板のＣｕｂｅ方位は９０度回転しても同一の構造であるため、０度、９０度の区別が無い。このため、板の曲げ加工方向を素材板の圧延方向と平行あるいは直角としても、Ｃｕｂｅ方位は同じ構造となり、良好な曲げ加工性が得られる。
　ただし、板の圧延方向が板の曲げ方向と４５度の方向になるなど、上記二つの方向以外の板の曲げ方向と板のＣｕｂｅ方位（配行方向）との関係では、Ｃｕｂｅ方位は変形中に回転し、結晶方位がランダム化して、曲げ加工性が劣る可能性があるため、曲げ加工を施す際における板の曲げ方向は、上記二つの方向とすることが好ましい。 The relationship between the bending direction and the Cube orientation (orientation direction) when bending the aluminum alloy plate is set so that the Cube orientation of the plate is parallel to the bending direction of the plate (the bending direction of the plate is the material plate). When the material is bent (parallel or perpendicular to the rolling direction), the Cube orientation during deformation becomes stable, and good bending workability is obtained. Since the Cube orientation of the plate has the same structure even when rotated 90 degrees, there is no distinction between 0 degrees and 90 degrees. For this reason, even if the bending direction of the plate is parallel or perpendicular to the rolling direction of the material plate, the Cube orientation has the same structure, and good bending workability can be obtained.
However, in the relationship between the bending direction of the plate other than the above two directions and the Cube orientation (distribution direction) of the plate, such as the rolling direction of the plate being 45 degrees with the bending direction of the plate, the Cube orientation is being deformed. Since the crystal orientation is randomized and the bending workability may be inferior, it is preferable that the bending direction of the plate when bending is the above two directions.
　なお、板表面におけるＣｕｂｅ方位分布密度の調整は、アルミニウム合金板におけるＳｉの含有量、Ｍｇの含有量、アルミニウム合金板の製造工程における熱間圧延条件、および冷間圧延の不実施によって達成される。 The adjustment of the Cube orientation distribution density on the surface of the plate is achieved by the Si content, the Mg content, the hot rolling conditions in the manufacturing process of the aluminum alloy plate, and the absence of cold rolling. .
（耐力：１８０ＭＰａ以上）
　本発明に係る接続部品用アルミニウム合金板の耐力（０．２％耐力）は、１８０ＭＰａ以上であることが好ましい。
　耐力が１８０ＭＰａ以上であると、接続部品に要求される耐クリープ性を確保することができる。一方、耐力が１８０ＭＰａ未満であると、耐クリープ性が低下してしまう。
　なお、耐クリープ性の確保という効果をより確実なものとするため、耐力は、好ましくは１９０ＭＰａ以上、さらに好ましくは１９５ＭＰａ以上である。 (Yield strength: 180 MPa or more)
The proof stress (0.2% proof stress) of the aluminum alloy plate for connecting parts according to the present invention is preferably 180 MPa or more.
When the proof stress is 180 MPa or more, the creep resistance required for the connecting parts can be ensured. On the other hand, when the yield strength is less than 180 MPa, the creep resistance is lowered.
In order to secure the effect of ensuring creep resistance, the yield strength is preferably 190 MPa or more, and more preferably 195 MPa or more.
　なお、耐力の調整は、アルミニウム合金板におけるＳｉの含有量、Ｍｇの含有量、アルミニウム合金板の製造工程における均質化熱処理条件、溶体化処理条件および人工時効処理条件によって達成される。 The adjustment of the proof stress is achieved by the Si content, the Mg content, the homogenization heat treatment condition, the solution treatment condition and the artificial aging treatment condition in the production process of the aluminum alloy sheet.
（接続部品）
　接続部品とは、複数の部材を電気的に接続する部品である。具体的には、電気を動力源とした各種電動輸送機器等に搭載されている、電池群、インバータ、モータ等の各種の電気機器間または電気機器内部の部品間を電気的に接続するバスバーである。
　そして、バスバーは、形状について特に限定されないが、所定の厚さを有するとともに、板状や角材状を呈する部品である。例えば、バスバーは、図１に示すような形状を呈する部品である。 (Connecting parts)
The connection component is a component that electrically connects a plurality of members. Specifically, it is a bus bar that is electrically connected to various electric devices such as battery groups, inverters, motors, etc. is there.
And although a bus bar is not specifically limited about a shape, while it has predetermined thickness, it is a component which exhibits plate shape or a square material shape. For example, the bus bar is a component having a shape as shown in FIG.
　ここで、アルミニウムは銅よりも導電率が低いことから、導電性能を確保するために、アルミニウム合金製のバスバーは、銅製のバスバーと比較して断面積を大きくしなければならない。部品の設置面積を考慮した場合には部品の幅寸法の増加は困難な場合が多く、板厚が増加することとなる。一般的に板厚が増加した場合には、曲げ表面での変形量が大きくなることから、アルミニウム合金から構成されるバスバーには、曲げ加工時における曲げ割れの発生という問題が生じる、つまり、曲げ加工性を向上させなければならないという課題が明確に現れることとなる。
　言い換えると、本発明に係る接続部品用アルミニウム合金板は、接続部品の中でも、厚さが１．５ｍｍ以上、特に、１．８～５．０ｍｍのバスバーに適用するのが好ましく、顕著な効果（耐クリープ性および曲げ加工性の両立という効果）を発揮することとなる。 Here, since aluminum has a lower conductivity than copper, the bus bar made of aluminum alloy has to have a larger cross-sectional area than the bus bar made of copper in order to ensure the conductive performance. When considering the installation area of the component, it is often difficult to increase the width of the component, and the plate thickness increases. In general, when the plate thickness increases, the amount of deformation on the bending surface increases, so the bus bar made of an aluminum alloy has a problem of occurrence of bending cracks during bending processing. The problem that workability must be improved will clearly appear.
In other words, the aluminum alloy plate for connection parts according to the present invention is preferably applied to a bus bar having a thickness of 1.5 mm or more, particularly 1.8 to 5.0 mm, among the connection parts, and has a remarkable effect ( Effect of achieving both creep resistance and bending workability).
　次に、第１実施形態に係る接続部品用アルミニウム合金板の製造方法について図２を参照しながら説明する。
［接続部品用アルミニウム合金板の製造方法］
　本発明に係る接続部品用アルミニウム合金板の製造方法は、均質化熱処理工程Ｓ２と、熱間圧延工程Ｓ３と、溶体化熱処理工程Ｓ４と、人工時効処理工程Ｓ５と、を含むことを特徴とする。
　以下、前記各工程を中心に説明する。 Next, the manufacturing method of the aluminum alloy plate for connection parts which concerns on 1st Embodiment is demonstrated, referring FIG.
[Method of manufacturing aluminum alloy plate for connecting parts]
The method for producing an aluminum alloy plate for connecting parts according to the present invention includes a homogenization heat treatment step S2, a hot rolling step S3, a solution heat treatment step S4, and an artificial aging treatment step S5. .
Hereinafter, the respective steps will be mainly described.
（鋳造工程）
　鋳造工程Ｓ１では、前記の成分組成であるアルミニウム合金を溶解し、ＤＣ鍛造法等の公知の鋳造法により鋳造し、アルミニウム合金の固相線温度未満まで冷却して厚さ４００～６００ｍｍ程度の鋳塊とし、必要に応じて面削を行う。 (Casting process)
In the casting step S1, the aluminum alloy having the above component composition is melted, cast by a known casting method such as a DC forging method, and cooled to below the solidus temperature of the aluminum alloy, and cast to a thickness of about 400 to 600 mm. Make a lump and chamfer as necessary.
（均質化熱処理工程）
　均質化熱処理工程Ｓ２では、鋳造工程Ｓ１で鋳造した鋳塊を圧延する前に、所定温度で均質化熱処理（均熱処理）を施す。鋳塊に均質化熱処理を施すことによって、内部応力が除去され、鋳造時に偏析した溶質元素が均質化され、また、鋳造冷却時やそれ以降に析出した金属間化合物が成長する。さらにこの均質化熱処理は、後続の熱間圧延工程Ｓ３のための予備加熱を兼ねるものである。
　均質化熱処理工程Ｓ２における熱処理温度（鋳塊温度）は５００～５７０℃である。熱処理温度が５００℃未満では、鋳造時に晶出したＳｉあるいはＭｇが未固溶のまま残存し、溶体化熱処理および人工時効処理後に適度な析出物分布を得ることができず、耐力および耐クリープ性が低下する。一方、５７０℃を超えると、鋳塊の表面で局部的な溶融（バーニング）が生じてしまう。さらに好ましくは、５６０℃以下である。
　均質化熱処理工程Ｓ２における熱処理時間（保持時間）は、均質化を完了させるためには１時間以上であればよく、製造効率の点から２４時間以内であればよい。 (Homogenization heat treatment process)
In the homogenization heat treatment step S2, homogenization heat treatment (soaking) is performed at a predetermined temperature before rolling the ingot cast in the casting step S1. By subjecting the ingot to homogenization heat treatment, internal stress is removed, solute elements segregated at the time of casting are homogenized, and intermetallic compounds precipitated at the time of casting cooling and thereafter grow. Further, the homogenization heat treatment also serves as preheating for the subsequent hot rolling step S3.
The heat treatment temperature (ingot temperature) in the homogenization heat treatment step S2 is 500 to 570 ° C. When the heat treatment temperature is less than 500 ° C., Si or Mg crystallized at the time of casting remains undissolved, and an appropriate precipitate distribution cannot be obtained after solution heat treatment and artificial aging treatment, yield strength and creep resistance. Decreases. On the other hand, when it exceeds 570 ° C., local melting (burning) occurs on the surface of the ingot. More preferably, it is 560 degrees C or less.
The heat treatment time (holding time) in the homogenization heat treatment step S2 may be 1 hour or longer in order to complete the homogenization, and may be within 24 hours from the viewpoint of production efficiency.
（熱間圧延工程）
　熱間圧延工程Ｓ３では、均質化熱処理工程Ｓ２から連続して、均質化された鋳塊を熱間圧延する。まず、均質化熱処理工程Ｓ２の熱処理完了時の温度を保持して鋳塊を粗圧延して、さらに仕上げ圧延により、所望の板厚の熱間圧延板（ホットコイル）とする。熱間圧延板の板厚は、アルミニウム合金板の最終板厚から逆算して設定すればよい。また、熱間圧延終了温度によりＣｕｂｅ方位分布密度を制御することができる。Ｃｕｂｅ方位分布密度を特に向上させて優れた曲げ加工性を得るためには、熱間圧延終了温度を３６０℃以下とし、熱間圧延終了時にも再結晶を抑制し、加工組織を残留させることが好ましく、３３０℃以下とするのが、さらに好ましい。 (Hot rolling process)
In the hot rolling step S3, the homogenized ingot is hot-rolled continuously from the homogenizing heat treatment step S2. First, the temperature at the time of completion of the heat treatment in the homogenization heat treatment step S2 is maintained, the ingot is roughly rolled, and further, hot rolled plate (hot coil) having a desired thickness is obtained by finish rolling. The thickness of the hot rolled sheet may be set by calculating back from the final thickness of the aluminum alloy sheet. Further, the Cube orientation distribution density can be controlled by the hot rolling end temperature. In order to improve the Cube orientation distribution density in particular and obtain excellent bending workability, the hot rolling end temperature should be 360 ° C. or less, and recrystallization is suppressed even at the end of hot rolling, and the processed structure remains. Preferably, the temperature is 330 ° C. or lower.
（溶体化熱処理工程）
　溶体化熱処理工程Ｓ４では、熱間圧延工程Ｓ３で製造した熱間圧延板を溶体化熱処理する。ここで、溶体化熱処理工程Ｓ４における熱処理温度（鋳塊温度）は５００～５７０℃である。熱処理温度が５００℃未満では、未固溶のＳｉあるいはＭｇが残存するため、溶体化熱処理および人工時効処理後に適度な析出物分布を得ることができず、所望の耐力および耐クリープ性を得ることができない。一方、５７０℃を超えると、板表面で局部的な溶融（バーニング）が生じてしまう。さらに好ましくは、５２０～５５０℃である。
　溶体化熱処理工程Ｓ４における前記熱処理温度での保持時間については、６０秒以内（０秒でもよい）である。６０秒を超えると、その効果が飽和するとともに生産性が低下してしまうからである。
　なお、熱間圧延工程Ｓ３の後に冷間圧延を施さないとともに、溶体化熱処理工程Ｓ４における熱処理温度を上記範囲とすることにより、Ｃｕｂｅ方位が適切に発達することとなり、板表面におけるＣｕｂｅ方位分布密度が所定値以上となる。 (Solution heat treatment process)
In the solution heat treatment step S4, the hot rolled plate manufactured in the hot rolling step S3 is solution heat treated. Here, the heat treatment temperature (ingot temperature) in the solution heat treatment step S4 is 500 to 570 ° C. When the heat treatment temperature is less than 500 ° C., undissolved Si or Mg remains, so that an appropriate precipitate distribution cannot be obtained after solution heat treatment and artificial aging treatment, and desired proof stress and creep resistance can be obtained. I can't. On the other hand, when it exceeds 570 ° C., local melting (burning) occurs on the plate surface. More preferably, it is 520 to 550 ° C.
The holding time at the heat treatment temperature in the solution heat treatment step S4 is within 60 seconds (may be 0 seconds). This is because if the time exceeds 60 seconds, the effect is saturated and the productivity is lowered.
In addition, by not performing cold rolling after the hot rolling step S3 and setting the heat treatment temperature in the solution heat treatment step S4 within the above range, the Cube orientation is appropriately developed, and the Cube orientation distribution density on the plate surface is increased. Becomes a predetermined value or more.
　溶体化熱処理工程Ｓ４において、２００℃から前記熱処理温度までの昇温速度は５℃／ｓ以上であることが好ましく、前記熱処理温度から２００℃までの降温速度は１０℃／ｓ以上であることが好ましい。
　昇温速度および降温速度を前記速度以上とすることにより、Ｃｕｂｅ方位が適切に発達するのをより確実なものとすることができる。 In the solution heat treatment step S4, the rate of temperature increase from 200 ° C. to the heat treatment temperature is preferably 5 ° C./s or more, and the rate of temperature decrease from the heat treatment temperature to 200 ° C. is 10 ° C./s or more. preferable.
By setting the rate of temperature rise and the rate of temperature fall to the above rate or more, it is possible to ensure that the Cube orientation is properly developed.
（人工時効処理工程）
　人工時効処理工程Ｓ５では、溶体化熱処理工程Ｓ４で溶体化熱処理を施した熱間圧延板に、所定温度・所定時間で人工時効処理を施す。
　人工時効処理工程Ｓ５における熱処理温度については、特に限定されないが１５０～２５０℃であることが好ましい。１５０℃未満であると所望の耐力、耐クリープ性を得ることができず、２５０℃を超えると析出物が粗大化して耐力、耐クリープ性が低下するからである。また、熱処理時間についても、特に限定されないが１～３０時間であることが好ましい。１時間未満であると特に量産時を想定した場合にはコイルあるいはシート内での不均一な温度分布を生じ、材料特性が不安定となりやすい。生産性を考慮して３０時間を上限とする。 (Artificial aging treatment process)
In the artificial aging treatment step S5, the artificial aging treatment is performed at a predetermined temperature and a predetermined time on the hot-rolled sheet subjected to the solution heat treatment in the solution heat treatment step S4.
The heat treatment temperature in the artificial aging treatment step S5 is not particularly limited, but is preferably 150 to 250 ° C. When the temperature is lower than 150 ° C., desired proof stress and creep resistance cannot be obtained, and when the temperature exceeds 250 ° C., precipitates are coarsened and the proof strength and creep resistance are lowered. Further, the heat treatment time is not particularly limited, but is preferably 1 to 30 hours. If the time is less than 1 hour, particularly when mass production is assumed, a non-uniform temperature distribution occurs in the coil or the sheet, and the material characteristics tend to become unstable. In consideration of productivity, the upper limit is 30 hours.
　本発明に係る接続部品用アルミニウム合金板の製造方法は、以上説明したとおりであるが、本発明を行うにあたり、前記各工程に悪影響を与えない範囲において、前記各工程の間あるいは前後に、他の工程を含めてもよい。例えば、人工時効処理工程Ｓ５の後に、所定の大きさに裁断する裁断工程や、図１に示すような所定の形状に加工（曲げ加工、穴抜き加工等）する加工工程を含めてもよい。
　また、前記各工程において、明示していない条件については、従来公知の条件を用いればよく、前記各工程での処理によって得られる効果を奏する限りにおいて、その条件を適宜変更できることは言うまでもない。 The manufacturing method of the aluminum alloy plate for connecting parts according to the present invention is as described above. However, in carrying out the present invention, other processes may be performed between or before and after the respective steps within a range that does not adversely affect the respective steps. These steps may be included. For example, after the artificial aging treatment step S5, a cutting step for cutting into a predetermined size or a processing step for processing into a predetermined shape (bending, punching, etc.) as shown in FIG. 1 may be included.
In addition, as for conditions that are not clearly shown in the respective steps, it is sufficient to use conventionally known conditions, and it is needless to say that the conditions can be appropriately changed as long as the effects obtained by the processing in the respective steps are exhibited.
　第２実施形態 Second embodiment
　以下、本発明に係る接続部品用アルミニウム合金板およびその製造方法を実施するための形態について、詳細に説明する。 Hereinafter, an embodiment for carrying out an aluminum alloy plate for connecting parts and a manufacturing method thereof according to the present invention will be described in detail.
　［接続部品用アルミニウム合金板］
　本発明に係る接続部品用アルミニウム合金板（以下、適宜、アルミニウム合金板という）は、所定量のＳｉおよびＭｇを含有し、残部がＡｌおよび不可避的不純物からなるアルミニウム合金で構成され、導電率、および板表面のＣｕｂｅ方位分布密度が所定値以上、結晶粒径が所定値以下であることを特徴とする。
　また、本発明に係る接続部品用アルミニウム合金板は、不可避的不純物のうちＦｅ、Ｚｎが所定値未満であることが好ましく、所定値未満のＣｕ、Ｍｎ、Ｃｒ、Ｚｒ、Ｔｉから選択される１種以上を含有することがさらに好ましい。
　以下、本発明に係る接続部品用アルミニウム合金板の板表面のＣｕｂｅ方位分布密度、および結晶粒径について数値限定した理由を説明する。なお、接続部品用アルミニウム合金板の各合金成分、および導電率は、第１実施形態と同様であるので説明を省略する。 [Aluminum alloy plate for connecting parts]
An aluminum alloy plate for connecting parts according to the present invention (hereinafter, appropriately referred to as an aluminum alloy plate) contains a predetermined amount of Si and Mg, and the balance is made of an aluminum alloy composed of Al and inevitable impurities, and has a conductivity, And the Cube orientation distribution density of the plate surface is not less than a predetermined value and the crystal grain size is not more than a predetermined value.
Further, the aluminum alloy plate for connecting parts according to the present invention preferably has Fe and Zn of unavoidable impurities less than a predetermined value, and is selected from Cu, Mn, Cr, Zr, and Ti that are less than a predetermined value. More preferably, it contains seeds or more.
The reason why the Cube orientation distribution density on the surface of the aluminum alloy plate for connecting parts according to the present invention and the crystal grain size are limited numerically will be described below. In addition, since each alloy component and electrical conductivity of the aluminum alloy plate for connection parts are the same as that of 1st Embodiment, description is abbreviate | omitted.
（Ｃｕｂｅ方位分布密度：２０以上）
　本発明に係る接続部品用アルミニウム合金板の板表面におけるＣｕｂｅ方位分布密度は２０以上とする。
　板表面におけるＣｕｂｅ方位分布密度が２０以上であることにより、接続部品に要求される耐クリープ性と曲げ加工性とを両立させることができる。一方、板表面におけるＣｕｂｅ方位分布密度が２０未満であると、曲げ加工性が低下してしまう。
なお、耐クリープ性および曲げ加工性の向上という効果をより確実なものとするため、Ｃｕｂｅ方位分布密度は、好ましくは３０以上、さらに好ましくは５０以上である。 (Cube orientation distribution density: 20 or more)
The Cube orientation distribution density on the plate surface of the aluminum alloy plate for connection parts according to the present invention is 20 or more.
When the Cube orientation distribution density on the surface of the plate is 20 or more, both creep resistance and bending workability required for connecting parts can be achieved. On the other hand, if the Cube orientation distribution density on the surface of the plate is less than 20, bending workability is deteriorated.
The Cube orientation distribution density is preferably 30 or more, and more preferably 50 or more, in order to ensure the effect of improving creep resistance and bending workability.
　なお、一般的な製造方法によれば、Ｃｕｂｅ方位分布密度は２０未満となるが、これは板表面の結晶方位が比較的ランダムであることを示す。
　一方、本発明が規定するように、Ｃｕｂｅ方位分布密度を２０以上とすると、つまり、Ｃｕｂｅ方位が一定量以上集積すると、隣り合う結晶粒との方位差の小さい小角粒界の割合が大きくなり、変形時の粒界段差を小さく、あるいは生じなくさせる。
　また、Ｃｕｂｅ方位においては、他の方位と比較して均一なすべり変形が可能になることからせん断帯の形成が抑制される。
　この結果、曲げ加工の際に割れの起点あるいは伝播経路となる粒界段差や結晶粒内でのせん断帯形成が抑制されるため、Ｃｕｂｅ方位分布密度を２０以上とすることにより、曲げ加工性を改善（向上）できる。
　なお、過度にＣｕｂｅ方位分布密度を高めようとすると、製造条件が厳しくなり生産性の低下を招くため、Ｃｕｂｅ方位分布密度は１００以下であるのが好ましい。 According to a general manufacturing method, the Cube orientation distribution density is less than 20, which indicates that the crystal orientation of the plate surface is relatively random.
On the other hand, as specified by the present invention, when the Cube orientation distribution density is 20 or more, that is, when the Cube orientation is accumulated more than a certain amount, the proportion of small-angle grain boundaries having a small orientation difference between adjacent crystal grains increases. Reduce or eliminate grain boundary step during deformation.
In addition, in the Cube orientation, since a uniform slip deformation is possible compared to other orientations, formation of a shear band is suppressed.
As a result, since the formation of a shear boundary in the grain boundary step and the crystal grain which becomes the starting point or propagation path of the crack during bending is suppressed, the bending workability can be improved by setting the Cube orientation distribution density to 20 or more. Can improve (improve).
If the Cube orientation distribution density is excessively increased, the manufacturing conditions become severe and the productivity is lowered. Therefore, the Cube orientation distribution density is preferably 100 or less.
　また、Ｃｕｂｅ方位分布密度を２０以上とすることで、同一レベルの耐力で比較した場合にも、接続部品に要求される耐クリープ性を良好にすることができる。この理由については必ずしも明確とはなっていないが、Ｃｕｂｅ方位はテイラー因子が小さく、転位の運動量が少ないことが知られており（崔祺(Sai Ki)ほか：軽金属,４９（１９９９）, Ｐ．５８３）、高温保持中の回復が抑制されることによるものと推定される。 Further, by setting the Cube orientation distribution density to 20 or more, even when compared with the same level of proof stress, the creep resistance required for the connecting parts can be improved. Although the reason for this is not necessarily clear, it is known that the Cube orientation has a small Taylor factor and a small momentum of dislocation (Sai ほ か Ki et al .: Light Metal, 49 (1999), P. 583), which is presumed to be due to suppression of recovery during high temperature holding.
（圧延方向の平均結晶粒径：１５０μｍ以下）
　本発明に係る接続部品用アルミニウム合金板は、板表面における圧延方向の平均結晶粒径が、１５０μｍ以下とする。
　圧延方向の平均結晶粒径が１５０μｍ以下であると、曲げ加工時における表面の品質を向上させることができる。一方、圧延方向の平均結晶粒径が１５０μｍを超えると曲げ加工時における表面に肌荒れや亀裂が発生する可能性が高くなる。
　なお、圧延方向の平均結晶粒径については、曲げ加工時の表面品質の向上という効果をより確実なものとするため、好ましくは１００μｍ以下、さらに好ましくは５０μｍ以下である。また、圧延方向の平均結晶粒径については、過度に小さくしようとすると、製造条件が厳しくなり生産性の低下を招くため、１０μｍ以上が好ましい。 (Average grain size in rolling direction: 150 μm or less)
The aluminum alloy plate for connecting parts according to the present invention has an average crystal grain size in the rolling direction on the plate surface of 150 μm or less.
When the average grain size in the rolling direction is 150 μm or less, the surface quality during bending can be improved. On the other hand, if the average crystal grain size in the rolling direction exceeds 150 μm, the possibility of rough skin and cracks on the surface during bending increases.
The average crystal grain size in the rolling direction is preferably 100 μm or less, and more preferably 50 μm or less, in order to ensure the effect of improving the surface quality during bending. Further, the average crystal grain size in the rolling direction is preferably 10 μm or more because manufacturing conditions become stricter and productivity is lowered when trying to make it excessively small.
　圧延方向の平均粒径は、アルミニウム合金板から測定片を切り出して、板表面を研磨し、電解液にてエッチングした後、光学顕微鏡にて１００倍程度で観察することにより測定することができる。 The average particle size in the rolling direction can be measured by cutting a measurement piece from an aluminum alloy plate, polishing the plate surface, etching it with an electrolytic solution, and observing it at about 100 times with an optical microscope.
　なお、圧延方向の平均結晶粒径は、アルミニウム合金板の製造工程における熱間圧延開始温度、圧延終了温度を制御することによって達成される。 The average grain size in the rolling direction is achieved by controlling the hot rolling start temperature and rolling end temperature in the aluminum alloy sheet manufacturing process.
　次に、第２実施形態に係る接続部品用アルミニウム合金板の製造方法について図２を参照しながら説明する。
［接続部品用アルミニウム合金板の製造方法］
　本発明に係る接続部品用アルミニウム合金板の製造方法は、均質化熱処理工程Ｓ２と、熱間圧延工程Ｓ３と、溶体化熱処理工程Ｓ４と、人工時効処理工程Ｓ５と、を含むことを特徴とする。
　以下、第１実施形態と異なる工程について説明する。他は、第１実施形態と同様であるので説明を省略する。 Next, the manufacturing method of the aluminum alloy plate for connection parts which concerns on 2nd Embodiment is demonstrated, referring FIG.
[Method of manufacturing aluminum alloy plate for connecting parts]
The method for producing an aluminum alloy plate for connecting parts according to the present invention includes a homogenization heat treatment step S2, a hot rolling step S3, a solution heat treatment step S4, and an artificial aging treatment step S5. .
Hereinafter, steps different from those of the first embodiment will be described. Since others are the same as that of 1st Embodiment, description is abbreviate | omitted.
（熱間圧延工程）
　熱間圧延工程Ｓ３では、均質化された鋳塊を熱間圧延する。このときの圧延開始温度を３５０～４５０℃とする。複数のパスからなる熱間圧延を施すことで、所望の板厚の熱間圧延板（ホットコイル）とする。 (Hot rolling process)
In the hot rolling step S3, the homogenized ingot is hot rolled. The rolling start temperature at this time is set to 350 to 450 ° C. By performing hot rolling consisting of a plurality of passes, a hot rolled plate (hot coil) having a desired thickness is obtained.
（均質化熱処理後の冷却の態様）
　ここで、均質化熱処理後に、熱間圧延を開始する３５０～４５０℃の温度範囲まで冷却する際の態様は、この温度範囲まで直接冷却し、この温度範囲で熱間圧延を開始しても良い（以下、２段均熱とも言う）。また、３５０℃以下の温度範囲まで冷却し、その後更に、熱間圧延を開始する３５０～４５０℃の温度範囲まで再加熱して、この温度範囲で熱間圧延を開始しても良い（以下、２回均熱とも言う）。 (Mode of cooling after homogenization heat treatment)
Here, after the homogenization heat treatment, the aspect of cooling to a temperature range of 350 to 450 ° C. where the hot rolling is started may be directly cooled to this temperature range and the hot rolling may be started within this temperature range. (Hereinafter also referred to as two-stage soaking). Alternatively, the temperature may be cooled to a temperature range of 350 ° C. or lower, and then reheated to a temperature range of 350 to 450 ° C. where hot rolling is started, and hot rolling may be started in this temperature range (hereinafter, Also called twice soaking).
　熱間圧延開始温度が４５０℃を超えた場合、曲げ加工時の肌荒れの原因となる。また、熱間圧延開始温度が３５０℃未満では、熱間圧延自体が困難となる。 When the hot rolling start temperature exceeds 450 ° C, it causes rough skin during bending. Moreover, if the hot rolling start temperature is less than 350 ° C., the hot rolling itself becomes difficult.
　後述するように、本発明では熱間圧延後に冷間圧延工程を施さないことを特徴とするため、熱間圧延板の組織制御が非常に重要である。特に、熱間圧延中に生じた再結晶粒は粗大となりやすく、この組織が溶体化熱処理後にも維持されるため、曲げ加工時の肌荒れの原因となることを見出した。熱間圧延開始温度を４５０℃以下とすることで、熱間圧延中の再結晶を抑制でき、その後の溶体化熱処理後の結晶粒径を所定値以下とすることができる。加えて、均質化熱処理後、熱間圧延開始温度までの冷却中に、鋳塊内にはＭｇ２Ｓｉ化合物が形成され、このＭｇ２Ｓｉ化合物が溶体化熱処理時の再結晶粒の核生成サイトとして働くため、結晶粒径を微細化することができる。 As will be described later, the present invention is characterized in that the cold rolling process is not performed after hot rolling, and thus the structure control of the hot rolled sheet is very important. In particular, the present inventors have found that recrystallized grains generated during hot rolling tend to be coarse and this structure is maintained even after solution heat treatment, which causes rough skin during bending. By setting the hot rolling start temperature to 450 ° C. or less, recrystallization during hot rolling can be suppressed, and the crystal grain size after the subsequent solution heat treatment can be set to a predetermined value or less. In addition, during the cooling to the hot rolling start temperature after the homogenization heat treatment, an Mg 2 Si compound is formed in the ingot, and this Mg 2 Si compound is a nucleation site of recrystallized grains during the solution heat treatment Therefore, the crystal grain size can be reduced.
　均質化熱処理後、熱間圧延開始温度範囲までの冷却速度は特に規定しないが、望ましくは２０～２００℃／ｈの範囲である。冷却速度が２０℃／ｈ以下となると、Ｍｇ２Ｓｉ化合物が粗大となるため、所望の強度を得るためにこれを再固溶させようとすると、溶体化熱処理が長時間必要となり、生産性が低下する。
　一方、冷却速度が２００℃／ｈと速くなりすぎると、鋳塊内での温度分布が不均一となり、熱収縮による変形やソリなどの異常が生じる新たな問題が発生する可能性もある。 Although the cooling rate to the hot rolling start temperature range after the homogenization heat treatment is not particularly specified, it is preferably in the range of 20 to 200 ° C./h. When the cooling rate is 20 ° C./h or less, the Mg 2 Si compound becomes coarse. Therefore, if it is attempted to re-solidify the Mg 2 Si compound in order to obtain a desired strength, a solution heat treatment is required for a long time, and productivity is increased. descend.
On the other hand, if the cooling rate is too high at 200 ° C./h, the temperature distribution in the ingot becomes non-uniform, and there is a possibility that a new problem in which an abnormality such as deformation or warping due to heat shrinkage occurs.
　また、冷却速度が速すぎると、均質化熱処理後、熱間圧延開始温度範囲まで冷却する間に形成されるＭｇ２Ｓｉ化合物の平均サイズが小さくなりすぎ、再結晶粒の核生成サイトとしての必要な、直径が２μｍ以上の比較的粗大なＭｇ２Ｓｉ化合物を、適当な数だけ分布させることができなくなるおそれがある。 On the other hand, if the cooling rate is too high, the average size of the Mg 2 Si compound formed while cooling to the hot rolling start temperature range after the homogenization heat treatment becomes too small, and it is necessary as a nucleation site for recrystallized grains. In addition, there is a possibility that an appropriate number of relatively coarse Mg 2 Si compounds having a diameter of 2 μm or more cannot be distributed.
 (均質化熱処理後の冷却手段)
　鋳塊を冷却する方法としては、例えば均熱炉内または炉外での強制ファン空冷、接触冷却、ミストやスプレーによる冷却がある。 (Cooling means after homogenization heat treatment)
As a method for cooling the ingot, there are, for example, forced fan air cooling in the soaking furnace or outside the furnace, contact cooling, and cooling by mist or spray.
　熱間圧延終了温度は特に規定しない。ただし、熱間圧延終了温度を特に３００℃以下に低温化することで、熱間圧延中の蓄積歪みを増加させ、その後の溶体化熱処理における再結晶駆動力を増加させることができるため、表面におけるＣｕｂｅ方位分布密度を高めると同時に、再結晶粒径を更に微細化することができる。 The hot rolling finish temperature is not specified. However, by lowering the hot rolling end temperature to 300 ° C. or less in particular, the accumulated strain during hot rolling can be increased and the recrystallization driving force in the subsequent solution heat treatment can be increased. The recrystallized grain size can be further refined while increasing the Cube orientation distribution density.
（溶体化熱処理工程）
　溶体化熱処理工程Ｓ４における前記熱処理温度での保持時間については、１００秒以内（０秒でもよい）である。１００秒を超えると、その効果が飽和するとともに生産性が低下してしまうからである。他は、第１実施形態と同様であるので説明を省略する。 (Solution heat treatment process)
The holding time at the heat treatment temperature in the solution heat treatment step S4 is within 100 seconds (may be 0 seconds). This is because when the time exceeds 100 seconds, the effect is saturated and the productivity is lowered. Since others are the same as that of 1st Embodiment, description is abbreviate | omitted.
　溶体化熱処理工程Ｓ４において、２００℃から前記熱処理温度までの昇温速度は５℃／ｓ以上であることが好ましく、前記熱処理温度から２００℃までの降温速度は１０℃／ｓ以上であることが好ましい。
　昇温速度を前記速度以上とすることにより、Ｃｕｂｅ方位が適切に発達するのをより確実なものとすることができる。また降温速度を前記速度以上とすることにより、所望の強度を確実に得ることができる。 In the solution heat treatment step S4, the rate of temperature increase from 200 ° C. to the heat treatment temperature is preferably 5 ° C./s or more, and the rate of temperature decrease from the heat treatment temperature to 200 ° C. is 10 ° C./s or more. preferable.
By setting the temperature rising rate to be equal to or higher than the above rate, it is possible to ensure that the Cube orientation is appropriately developed. Moreover, desired intensity | strength can be acquired reliably by making temperature-fall rate more than the said speed | rate.
　第１実施例（第１実施形態の実施例） Example 1 (Example of the first embodiment)
　次に、本発明に係る接続部品用アルミニウム合金板およびその製造方法について、本発明の要件を満たす実施例と本発明の要件を満たさない比較例とを比較して具体的に説明する。
［供試材の作製］
　表１に示す組成のアルミニウム合金（合金１～１７）を、溶解し、半連続鋳造にて鋳塊を作製し、面削処理をした。この鋳塊に、表２に示す条件で均質化熱処理を行ったのち、冷却することなく連続して、圧延率９９％の熱間圧延を施して（熱間圧延終了温度は表２）、熱間圧延板とした。その後、冷間圧延を施さず（供試材２０、２１は冷間圧延を施し）、表２に示す条件で溶体化熱処理を行った。そして、溶体化熱処理後、２００℃、２時間保持する人工時効処理を施す（供試材２０は施さない）ことで、供試材（厚さ２ｍｍ）を作製した。 Next, the aluminum alloy plate for connecting parts and the manufacturing method thereof according to the present invention will be specifically described by comparing an example satisfying the requirements of the present invention with a comparative example not satisfying the requirements of the present invention.
[Production of test materials]
Aluminum alloys (alloys 1 to 17) having the compositions shown in Table 1 were melted, ingots were produced by semi-continuous casting, and face machining was performed. The ingot was subjected to homogenization heat treatment under the conditions shown in Table 2, and then subjected to hot rolling at a rolling rate of 99% continuously without cooling (hot rolling end temperature is Table 2). A rolled sheet was used. Thereafter, cold rolling was not performed (the test materials 20 and 21 were cold rolled), and solution heat treatment was performed under the conditions shown in Table 2. Then, after the solution heat treatment, a sample material (thickness 2 mm) was produced by performing an artificial aging treatment (not performed on the sample material 20) that is held at 200 ° C. for 2 hours.
［評価］
（引張試験）
　供試材から引張方向が圧延方向と平行になるようにＪＩＳ５号の試験片を切り出した。この試験片を用いて、ＪＩＳ Ｚ ２２４１に準拠して引張試験を実施し、引張強さ、耐力（０．２％耐力）、および伸びを測定した。
　なお、クロスヘッド速度は５ｍｍ／分で、試験片が破断するまで一定の速度で行った。 [Evaluation]
(Tensile test)
A test piece of JIS No. 5 was cut out from the specimen so that the tensile direction was parallel to the rolling direction. Using this test piece, a tensile test was performed in accordance with JIS Z 2241, and tensile strength, yield strength (0.2% yield strength), and elongation were measured.
The crosshead speed was 5 mm / min, and the test was performed at a constant speed until the test piece broke.
（Ｃｕｂｅ方位分布密度）
　作製した供試材の表面を、株式会社リガク製のＸ線回折装置［型式「リガクＲＡＤ－ｒＸ」（Ｒｕ－２００Ｂ）］を用いて計測することで、Ｃｕｂｅ方位分布密度を求めた。当該Ｘ線回折装置を用いて不完全極点図によるＯＤＦ解析を行った。詳細には、ｓｃｈｌｕｚの反射法により、｛１００｝面、｛１１１｝面の不完全極点図を作成し、Ｂｕｎｇｅの反復級数展開法（ｐｏｓｉｔｉｖｉｔｙ法）を適用してＯＤＦ解析を実施し、Ｃｕｂｅ方位分布密度を求めた。 (Cube orientation distribution density)
Cube orientation distribution density was determined by measuring the surface of the prepared specimen using an X-ray diffractometer manufactured by Rigaku Corporation [model “Rigaku RAD-rX” (Ru-200B)]. ODF analysis was performed using an incomplete pole figure using the X-ray diffractometer. In detail, the incomplete pole figure of {100} plane and {111} plane is created by schluz reflection method, ODF analysis is performed by applying Bunge's iterative series expansion method (positivity method), and Cube orientation The distribution density was determined.
（導電率）
　導電率の測定は、日本フェルスター株式会社(FOERSTER JAPAN Limited)製の渦流導電率測定装置［型式「シグマテストＤ２．０６８」］によって測定した。また、導電率の測定は、供試材表面の互いに間隔を１００ｍｍ以上開けた任意の５箇所で行った。そして、本発明における導電率は、測定された各導電率を平均化したものとした。 (conductivity)
The conductivity was measured by an eddy current conductivity measuring device [model “Sigma Test D2.068”] manufactured by FOERSTER JAPAN Limited. In addition, the measurement of the conductivity was performed at any five locations on the surface of the test material with a space of 100 mm or more between each other. The electrical conductivity in the present invention is obtained by averaging the measured electrical conductivities.
（曲げ加工性）
　供試材から試験片長手方向が圧延方向と一致するようにＪＩＳ３号（ＪＩＳ Ｚ ２２０４）の試験片を切り出した。この試験片を、ＪＩＳ Ｚ ２２４８に準拠してＶブロック法により曲げ試験を実施し（図３参照）、曲げ加工性を評価した。なお、曲げ試験は、θ（曲げ角度）：９０°、ｒ（内側曲げ半径）：０ｍｍ、ｔ（供試材板厚）：２ｍｍ、という条件で実施した。
　曲げ試験後の曲げ部（湾曲部、幅：３０ｍｍ）の割れの発生状況を観察し、５枚の試験片のうち、全ての試験片において亀裂長さ２ｍｍ以上の曲げ割れが確認できなかったものを極めて良好（○）、いずれか１枚以上に割れが生じた場合を良好（△）、全ての試験片に割れが生じてしまった場合を不良（×）と評価した。 (Bending workability)
A test piece of JIS No. 3 (JIS Z 2204) was cut out from the specimen so that the longitudinal direction of the test piece coincided with the rolling direction. The test piece was subjected to a bending test by the V-block method according to JIS Z 2248 (see FIG. 3), and the bending workability was evaluated. The bending test was performed under the conditions of θ (bending angle): 90 °, r (inner bending radius): 0 mm, and t (test material plate thickness): 2 mm.
Observation of the occurrence of cracks in the bent part (curved part, width: 30 mm) after the bending test, and bending cracks with a crack length of 2 mm or more could not be confirmed in all of the five test pieces Was extremely good (◯), the case where any one or more cracks occurred was evaluated as good (Δ), and the case where all the test pieces were cracked was evaluated as defective (×).
（残留応力比）
　残留応力比は、日本電子材料工業会(Japan Electronics and Information Technology Industries Association)標準規格ＥＭＡＳ－３００３に記載の片持ち梁方式により測定した。
　詳細には、試験片長手方向が圧延方向に対して直角となるように幅１０ｍｍ、長さ２５０ｍｍの短冊状の試験片（供試材板厚：２ｍｍ）を切り出した。その試験片の一端を剛体試験台に固定した。試験片に、スパン１５０ｍｍ、初期変形量（δ０＝１０ｍｍ）を付与し、その状態のまま１２０℃で１００時間保持した後、応力を除去して試験片の変形量（ε）を測定した。残留応力比は、「残留応力比＝（δ０－ε）÷δ０×１００」で求めた。この残留応力比の値が７５％以上のものを、高温時の持続的な応力により変形する現象（クリープ）に対して耐える性能を有する、つまり、接続部品に要求される耐クリープ性を有すると評価した。 (Residual stress ratio)
The residual stress ratio was measured by the cantilever method described in the Japan Electronics and Information Technology Industries Association standard EMAS-3003.
Specifically, a strip-shaped test piece (sample thickness: 2 mm) having a width of 10 mm and a length of 250 mm was cut out so that the longitudinal direction of the test piece was perpendicular to the rolling direction. One end of the test piece was fixed to a rigid test table. The test piece was given a span of 150 mm and an initial deformation amount (δ0 = 10 mm), held in that state at 120 ° C. for 100 hours, and then the stress was removed to measure the deformation amount (ε) of the test piece. The residual stress ratio was determined by “residual stress ratio = (δ0−ε) ÷ δ0 × 100”. When the residual stress ratio value is 75% or more, it has the ability to withstand the phenomenon (creep) that is deformed by continuous stress at high temperature, that is, it has the creep resistance required for connecting parts. evaluated.
　詳細なアルミニウム合金の成分、供試材の製造条件、および材料特性（試験結果）を表１または表２に示す。なお、表１、２において、本発明の構成を満たさないものについては、数値に下線を引いて示す。 Table 1 or 2 shows the detailed components of the aluminum alloy, the production conditions of the test material, and the material characteristics (test results). In Tables 1 and 2, numerical values that do not satisfy the configuration of the present invention are underlined.
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000002
Figure JPOXMLDOC01-appb-T000002
［結果の検討］
　供試材１～９については、本発明の規定する要件を全て満たしていることから、内曲げＲ＝０ｍｍと非常に厳しい曲げ加工条件とした場合にも、曲げ加工性が極めて良好（○）または良好（△）という評価となるとともに、接続部品に要求される耐クリープ性を有するという評価となった。 [Examination of results]
Since the specimens 1 to 9 satisfy all the requirements stipulated by the present invention, the bending workability is very good even when the internal bending R = 0 mm and very severe bending conditions (◯). Or, it was evaluated as good (Δ) and evaluated as having creep resistance required for the connecting parts.
　供試材１０（合金９）は、Ｓｉの含有量が本発明で規定する数値範囲の下限値未満であるとともに、Ｍｇの含有量が本発明で規定する数値範囲の上限値を超えていたため、耐力が所定値以上とならず、その結果、曲げ加工性および耐クリープ性に優れないという評価となった。 The specimen 10 (alloy 9) had a Si content that was less than the lower limit of the numerical range defined in the present invention, and the Mg content exceeded the upper limit of the numerical range defined in the present invention. The proof stress did not exceed a predetermined value, and as a result, the evaluation was that the bending workability and creep resistance were not excellent.
　供試材１１（合金１０）は、Ｓｉの含有量が本発明で規定する数値範囲の上限値を超えるとともに、Ｍｇの含有量が本発明で規定する数値範囲の下限値未満であったため、耐力が所定値以上とならないとともに、曲げ加工性および耐クリープ性に優れないという評価となった。 In the test material 11 (alloy 10), the Si content exceeded the upper limit of the numerical range defined in the present invention, and the Mg content was less than the lower limit of the numerical range defined in the present invention. Was not higher than the predetermined value, and the bending workability and creep resistance were not excellent.
　供試材１２～１８（合金１１～１７）は、Ｆｅ、Ｚｎ、Ｃｕ、Ｍｎ、Ｃｒ、Ｚｒ、Ｔｉのうち、いずれか一つが本発明で規定する数値以上となっていたため、曲げ加工性が不良（×）という評価となった。 Since each of the test materials 12 to 18 (alloys 11 to 17) had a value greater than the value specified in the present invention, any one of Fe, Zn, Cu, Mn, Cr, Zr, and Ti had bending workability. The evaluation was bad (×).
　供試材１９は、均質化熱処理の熱処理温度が本発明で規定する数値範囲の上限値を超えてしまったため、バーニングが発生してしまい、以降の製造および試験を行うことができなくなった。 Since the heat treatment temperature of the homogenization heat treatment exceeded the upper limit value of the numerical value range defined in the present invention, the test material 19 was burned and could not be manufactured and tested thereafter.
　供試材２０、２１は、冷間圧延を行ったため、Ｃｕｂｅ方位分布密度が所定値未満となってしまい、その結果、曲げ加工性が不良（×）という結果となった。さらに、供試材２０については、溶体化熱処理としてバッチ炉焼鈍（２４０℃×５時間（昇温速度：５０℃／時間、降温速度：５０℃／時間））を行ったために、耐クリープ性に優れないという評価となった。 Since the test materials 20 and 21 were cold-rolled, the Cube orientation distribution density was less than a predetermined value, resulting in poor bending workability (x). Furthermore, since the sample material 20 was subjected to batch furnace annealing (240 ° C. × 5 hours (temperature increase rate: 50 ° C./hour, temperature decrease rate: 50 ° C./hour)) as a solution heat treatment, the creep resistance was improved. The evaluation was not good.
　供試材２２は、溶体化熱処理の熱処理温度が本発明で規定する数値範囲の上限値を超えてしまったため、バーニングが発生してしまい、以降の製造および試験を行うことができなくなった。 Since the heat treatment temperature of the solution heat treatment exceeded the upper limit of the numerical range defined in the present invention, the test material 22 was burned, and the subsequent manufacturing and testing could not be performed.
　なお、供試材２０は、特許文献２に記載されたアルミニウム合金板を想定したものであり、供試材２１は、特許文献１に記載されたアルミニウム合金板を想定したものである。 In addition, the sample material 20 assumes the aluminum alloy plate described in Patent Document 2, and the sample material 21 assumes the aluminum alloy plate described in Patent Document 1.
　第２実施例（第２実施形態の実施例） Second example (Example of the second embodiment)
　次に、本発明に係る接続部品用アルミニウム合金板およびその製造方法について、本発明の要件を満たす実施例と本発明の要件を満たさない比較例とを比較して具体的に説明する。なお、第１実施形態と異なる点を説明し、その他は第１実施形態と同様であるので説明を省略する。
［供試材の作製］
　表１に示す組成のアルミニウム合金（合金１～１７）を、溶解し、半連続鋳造にて鋳塊を作製し、面削処理をした。この鋳塊に、表３に示す条件で均質化熱処理を行ったのち、冷却することなく連続して、圧延率９９％の熱間圧延を施して（熱間圧延終了温度は表３）、熱間圧延板とした。その後、冷間圧延を施さず（供試材２４、２５は冷間圧延を施し）、表３に示す条件で溶体化熱処理を行った。そして、溶体化熱処理後、２００℃、２時間保持する人工時効処理を施す（供試材２４は施さない）ことで、供試材（厚さ２ｍｍ）を作製した。
　なお、供試材１～４については、熱間圧延を２段均熱で行い、供試材５～１８、２０、２３については、熱間圧延を２回均熱で行った。 Next, the aluminum alloy plate for connecting parts and the manufacturing method thereof according to the present invention will be specifically described by comparing an example satisfying the requirements of the present invention with a comparative example not satisfying the requirements of the present invention. The differences from the first embodiment will be described, and the other points are the same as those of the first embodiment, and the description thereof will be omitted.
[Production of test materials]
Aluminum alloys (alloys 1 to 17) having the compositions shown in Table 1 were melted, ingots were produced by semi-continuous casting, and face machining was performed. This ingot was subjected to homogenization heat treatment under the conditions shown in Table 3, and then subjected to hot rolling at a rolling rate of 99% continuously without cooling (hot rolling end temperature is Table 3). A rolled sheet was used. Thereafter, cold rolling was not performed (the specimens 24 and 25 were cold rolled), and solution heat treatment was performed under the conditions shown in Table 3. Then, after the solution heat treatment, a test material (thickness 2 mm) was prepared by performing an artificial aging treatment (not applied to the test material 24) held at 200 ° C. for 2 hours.
For the test materials 1 to 4, hot rolling was performed by two-stage soaking, and for the test materials 5 to 18, 20, and 23, hot rolling was performed twice by soaking.
（平均結晶粒径の測定）
　供試材表面を研磨し、この研磨した面を電解液にてエッチングして、光学顕微鏡にて１００倍で写真撮影した。この顕微鏡写真で、切片法により圧延方向の結晶粒径を測定した。結晶粒径は５箇所で測定し、平均値を表３に示す。 (Measurement of average crystal grain size)
The surface of the test material was polished, the polished surface was etched with an electrolytic solution, and photographed with an optical microscope at a magnification of 100. With this micrograph, the crystal grain size in the rolling direction was measured by the section method. The crystal grain size was measured at five locations, and the average value is shown in Table 3.
（曲げ加工性）
　曲げ試験後の曲げ部（湾曲部、幅：３０ｍｍ）の割れの発生状況を観察し、５枚の試験片のうち、全ての試験片において肌荒れおよび割れとも発生しなかったものを極めて良好（○）、いずれか１枚以上に許容レベルのわずかな肌荒れが生じたものを良好（△）、顕著な肌荒れが発生したもの（×）、または亀裂長さ２ｍｍ以上の割れが生じたものを不良（××）と評価した。他は、第１実施形態と同様であるので説明を省略する。 (Bending workability)
Observe the occurrence of cracks in the bent part (curved part, width: 30 mm) after the bending test, and among the five test pieces, all of the test pieces that did not generate rough skin or cracks were very good (○ ), One with at least one acceptable level of rough skin is good (△), marked with rough skin (×), or cracked with a crack length of 2 mm or more is defective ( Xx). Since others are the same as that of 1st Embodiment, description is abbreviate | omitted.
　詳細なアルミニウム合金の成分、供試材の製造条件、および材料特性（試験結果）を表１または表３に示す。なお、表１、３において、本発明の構成を満たさないものについては、数値に下線を引いて示す。 Table 1 or Table 3 shows detailed aluminum alloy components, production conditions of the test materials, and material characteristics (test results). In Tables 1 and 3, numerical values that do not satisfy the configuration of the present invention are underlined.
Figure JPOXMLDOC01-appb-T000003
Figure JPOXMLDOC01-appb-T000003
［結果の検討］
　試供材１から１９については、第１実施形態と同様であるので説明を省略する。ただし、供試材１２～１８（合金１１～１７）は、Ｆｅ、Ｚｎ、Ｃｕ、Ｍｎ、Ｃｒ、Ｚｒ、Ｔｉのうち、いずれか一つが本発明で規定する数値以上となっていたため、曲げ加工性が不良（××）という評価となった。 [Examination of results]
Since the sample materials 1 to 19 are the same as those in the first embodiment, description thereof will be omitted. However, in the specimens 12 to 18 (alloys 11 to 17), any one of Fe, Zn, Cu, Mn, Cr, Zr, and Ti had a numerical value defined by the present invention. It became evaluation that property was bad (xx).
　供試材２０は、溶体化熱処理の熱処理温度が本発明で規定する数値範囲の上限値を超えてしまったため、バーニングが発生してしまい、以降の製造および試験を行うことができなくなった。 Since the heat treatment temperature of the solution heat treatment exceeded the upper limit of the numerical range defined in the present invention, the test material 20 was burned, and the subsequent manufacturing and testing could not be performed.
　供試材２１、２２は、熱間圧延の開始温度が本発明で規定する数値範囲の上限値を超えてしまったため、圧延方向の平均結晶粒径が所定値を超えてしまい、その結果、曲げ加工性が不良という結果となった。一方、供試材２３は、熱間圧延の開始温度が本発明で規定する数値範囲の下限値未満であったため、熱間圧延が困難となり、以降の製造および試験を行うことができなくなった。 In the test materials 21 and 22, since the starting temperature of hot rolling exceeded the upper limit of the numerical range defined in the present invention, the average crystal grain size in the rolling direction exceeded a predetermined value, and as a result, bending The processability was poor. On the other hand, since the start temperature of the hot rolling was less than the lower limit value of the numerical range specified in the present invention, the hot rolling became difficult and the subsequent production and test could not be performed.
　供試材２４、２５は、冷間圧延を行ったため、Ｃｕｂｅ方位分布密度が所定値未満となってしまい、その結果、曲げ加工性が不良という結果となった。さらに、供試材２４については、溶体化熱処理としてバッチ炉焼鈍（２４０℃×５時間（昇温速度：５０℃／時間、降温速度：５０℃／時間））を行ったために、耐クリープ性に優れないという評価となった。 Since the specimens 24 and 25 were cold-rolled, the Cube orientation distribution density was less than a predetermined value, resulting in poor bending workability. Furthermore, since the sample material 24 was subjected to batch furnace annealing (240 ° C. × 5 hours (temperature increase rate: 50 ° C./hour, temperature decrease rate: 50 ° C./hour)) as a solution heat treatment, the creep resistance was improved. The evaluation was not good.
　なお、供試材２４は、特許文献２に記載されたアルミニウム合金板を想定したものであり、供試材２５は、特許文献１に記載されたアルミニウム合金板を想定したものである。 In addition, the sample material 24 assumes the aluminum alloy plate described in Patent Document 2, and the sample material 25 assumes the aluminum alloy plate described in Patent Document 1.
　　１　接続部品（バスバー）
　　１ａ　連結部 1 Connecting parts (bus bar)
1a connecting part

Claims (10)

  1. 　Ｓｉ：０．３～１．５質量％、Ｍｇ：０．３～１．０質量％を含有し、残部がＡｌおよび不可避的不純物からなるアルミニウム合金で構成され、
    　導電率が４５．０％ＩＡＣＳ以上であり、結晶方位分布関数解析による板表面のＣｕｂｅ方位分布密度が１５以上であることを特徴とする接続部品用アルミニウム合金板。     Si: 0.3 to 1.5% by mass, Mg: 0.3 to 1.0% by mass, with the balance being made of an aluminum alloy consisting of Al and inevitable impurities,
    An aluminum alloy plate for connecting parts, wherein the conductivity is 45.0% IACS or more, and the Cube orientation distribution density on the plate surface by a crystal orientation distribution function analysis is 15 or more.
  2. 　前記不可避的不純物のうち、Ｆｅ：０．５質量％未満、Ｚｎ：０．５質量％未満であることを特徴とする請求項１に記載の接続部品用アルミニウム合金板。 The aluminum alloy plate for connecting parts according to claim 1, wherein among the inevitable impurities, Fe: less than 0.5 mass%, Zn: less than 0.5 mass%.
  3. 　前記アルミニウム合金が、Ｃｕ：１．０質量％未満、Ｍｎ：１．０質量％未満、Ｃｒ：０．５質量％未満、Ｚｒ：０．３質量％未満、Ｔｉ：０．１質量％未満、から選択される１種以上をさらに含有することを特徴とする請求項１に記載の接続部品用アルミニウム合金板。 The aluminum alloy is Cu: less than 1.0 mass%, Mn: less than 1.0 mass%, Cr: less than 0.5 mass%, Zr: less than 0.3 mass%, Ti: less than 0.1 mass%, The aluminum alloy plate for connection parts according to claim 1, further comprising at least one selected from the group consisting of:
  4. 　前記アルミニウム合金が、Ｃｕ：１．０質量％未満、Ｍｎ：１．０質量％未満、Ｃｒ：０．５質量％未満、Ｚｒ：０．３質量％未満、Ｔｉ：０．１質量％未満、から選択される１種以上をさらに含有することを特徴とする請求項２に記載の接続部品用アルミニウム合金板。 The aluminum alloy is Cu: less than 1.0 mass%, Mn: less than 1.0 mass%, Cr: less than 0.5 mass%, Zr: less than 0.3 mass%, Ti: less than 0.1 mass%, The aluminum alloy plate for connection parts according to claim 2, further comprising at least one selected from the group consisting of:
  5. 　前記結晶方位分布関数解析による板表面のＣｕｂｅ方位分布密度が２０以上、板表面における圧延方向の平均結晶粒径が１５０μｍ以下であることを特徴とする請求項１に記載の接続部品用アルミニウム合金板。 The aluminum alloy plate for connecting parts according to claim 1, wherein the Cube orientation distribution density on the plate surface by the crystal orientation distribution function analysis is 20 or more and the average crystal grain size in the rolling direction on the plate surface is 150 µm or less. .
  6. 　前記不可避的不純物のうち、Ｆｅ：０．５質量％未満、Ｚｎ：０．５質量％未満であることを特徴とする請求項５に記載の接続部品用アルミニウム合金板。 6. The aluminum alloy plate for connecting parts according to claim 5, wherein among the inevitable impurities, Fe: less than 0.5 mass% and Zn: less than 0.5 mass%.
  7. 　前記アルミニウム合金が、Ｃｕ：１．０質量％未満、Ｍｎ：１．０質量％未満、Ｃｒ：０．５質量％未満、Ｚｒ：０．３質量％未満、Ｔｉ：０．１質量％未満、から選択される１種以上をさらに含有することを特徴とする請求項５に記載の接続部品用アルミニウム合金板。 The aluminum alloy is Cu: less than 1.0 mass%, Mn: less than 1.0 mass%, Cr: less than 0.5 mass%, Zr: less than 0.3 mass%, Ti: less than 0.1 mass%, The aluminum alloy plate for connection parts according to claim 5, further comprising at least one selected from the group consisting of:
  8. 　前記アルミニウム合金が、Ｃｕ：１．０質量％未満、Ｍｎ：１．０質量％未満、Ｃｒ：０．５質量％未満、Ｚｒ：０．３質量％未満、Ｔｉ：０．１質量％未満、から選択される１種以上をさらに含有することを特徴とする請求項６に記載の接続部品用アルミニウム合金板。 The aluminum alloy is Cu: less than 1.0 mass%, Mn: less than 1.0 mass%, Cr: less than 0.5 mass%, Zr: less than 0.3 mass%, Ti: less than 0.1 mass%, The aluminum alloy plate for connection parts according to claim 6, further comprising at least one selected from the group consisting of:
  9. 　請求項１乃至請求項４のいずれか１項に記載の前記アルミニウム合金からなる鋳塊に５００～５７０℃、１～２４時間の均質化熱処理を施す均質化熱処理工程と、
    　前記均質化熱処理を施した鋳塊に熱間圧延を施して熱間圧延板を製造する熱間圧延工程と、
    　前記熱間圧延板に冷間圧延を施さずに、５００～５７０℃、６０秒以下保持する溶体化熱処理を施す溶体化熱処理工程と、
    　前記溶体化熱処理を施した熱間圧延板に人工時効処理を施す人工時効処理工程と、
    　を含むことを特徴とする接続部品用アルミニウム合金板の製造方法。     A homogenization heat treatment step of subjecting the ingot made of the aluminum alloy according to any one of claims 1 to 4 to a homogenization heat treatment at 500 to 570 ° C for 1 to 24 hours,
    A hot rolling step of producing a hot rolled sheet by subjecting the ingot subjected to the homogenizing heat treatment to hot rolling;
    A solution heat treatment step of subjecting the hot-rolled sheet to a solution heat treatment that is held at 500 to 570 ° C. for 60 seconds or less without cold rolling;
    An artificial aging treatment step of performing an artificial aging treatment on the hot-rolled sheet subjected to the solution heat treatment;
    The manufacturing method of the aluminum alloy plate for connection components characterized by including this.
  10. 　請求項５乃至請求項８のいずれか１項に記載の前記アルミニウム合金からなる鋳塊に５００～５７０℃、１～２４時間の均質化熱処理を施す均質化熱処理工程と、
    　前記均質化熱処理を施した鋳塊に圧延開始温度を３５０～４５０℃とした複数のパスからなる圧延を施して熱間圧延板を製造する熱間圧延工程と、
    　前記熱間圧延板に冷間圧延を施さずに、５００～５７０℃、１００秒以下保持する溶体化熱処理を施す溶体化熱処理工程と、
    　前記溶体化熱処理を施した熱間圧延板に人工時効処理を施す人工時効処理工程と、
    　を含むことを特徴とする接続部品用アルミニウム合金板の製造方法。     A homogenization heat treatment step of subjecting the ingot made of the aluminum alloy according to any one of claims 5 to 8 to a homogenization heat treatment at 500 to 570 ° C for 1 to 24 hours,
    A hot rolling step of producing a hot-rolled sheet by subjecting the ingot subjected to the homogenization heat treatment to rolling comprising a plurality of passes at a rolling start temperature of 350 to 450 ° C .;
    A solution heat treatment step of subjecting the hot rolled sheet to a solution heat treatment that is maintained at 500 to 570 ° C. for 100 seconds or less without performing cold rolling;
    An artificial aging treatment step of performing an artificial aging treatment on the hot-rolled sheet subjected to the solution heat treatment;
    The manufacturing method of the aluminum alloy plate for connection components characterized by including this.
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