US20120321507A1 - Aluminum alloy conductor - Google Patents

Aluminum alloy conductor Download PDF

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Publication number
US20120321507A1
US20120321507A1 US13/594,480 US201213594480A US2012321507A1 US 20120321507 A1 US20120321507 A1 US 20120321507A1 US 201213594480 A US201213594480 A US 201213594480A US 2012321507 A1 US2012321507 A1 US 2012321507A1
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aluminum alloy
conductor
wire
intermetallic compound
alloy conductor
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Shigeki Sekiya
Kyota Susai
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Furukawa Electric Co Ltd
Furukawa Automotive Systems Inc
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Furukawa Electric Co Ltd
Furukawa Automotive Systems Inc
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Assigned to FURUKAWA ELECTRIC CO., LTD., FURUKAWA AUTOMOTIVE SYSTEMS INC. reassignment FURUKAWA ELECTRIC CO., LTD. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: SEKIYA, SHIGEKI, SUSAI, KYOTA
Publication of US20120321507A1 publication Critical patent/US20120321507A1/en
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    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
    • B21C1/003—Drawing materials of special alloys so far as the composition of the alloy requires or permits special drawing methods or sequences
    • 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
    • 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
    • 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

Definitions

  • the present invention relates to an aluminum alloy conductor that is used as a conductor of an electrical wiring.
  • a member in which a terminal (connector) made of copper or a copper alloy (for example, brass) is attached to electrical wires composed of conductors of copper or a copper alloy, which is called a wire harness, has been used as an electrical wiring for movable bodies, such as automobiles, trains, and aircrafts.
  • a wire harness a member in which a terminal (connector) made of copper or a copper alloy (for example, brass) is attached to electrical wires composed of conductors of copper or a copper alloy, which is called a wire harness
  • the specific gravity of aluminum is about one-third of that of copper, and the electrical conductivity of aluminum is about two-thirds of that of copper (when pure copper is considered as a criterion of 100% IACS, pure aluminum has about 66% IACS). Therefore, in order to pass a current through a conductor of pure aluminum, in which the intensity of the current is identical to that through a conductor of pure copper, it is necessary to adjust the cross-sectional area of the conductor of pure aluminum to about 1.5 times larger than that of the conductor of pure copper, but aluminum conductor is still more advantageous than copper conductor in that the former has an about half weight of the latter.
  • % IACS represents an electrical conductivity when the resistivity 1.7241 ⁇ 10 ⁇ 8 ⁇ m of International Annealed Copper Standard is defined as 100% IACS.
  • an aluminum conductor that is used in an electrical wiring of a movable body a material is required, which is excellent in mechanical strength and flexibility that are required in handling and attaching, and which is excellent in electrical conductivity that is required for passing much electricity, as well as which is excellent in resistance to bending fatigue.
  • Typical aluminum conductors used in electrical wirings of movable bodies include those described in Patent Literatures 1 to 4. However, as mentioned below, the inventions described in the patent literatures each have a further problem to be solved.
  • Patent Literature 1 Since the invention described in Patent Literature 1 does not conduct finish annealing, flexibility that is required for operations of attaching in a vehicle body cannot be ensured.
  • Patent Literature 2 discloses finish annealing, but the condition therefor is different from a condition by which intermetallic compounds can be controlled so as to improve resistance to bending fatigue, electrical conductivity and the like while keeping excellent flexibility.
  • Patent Literature 4 contains antimony (Sb) as an additive element, and thus is a technique that is being substituted by an alternate product in view of environmental load.
  • Sb antimony
  • Patent Literature 1 JP-A-2006-19163 (“JP-A” means unexamined published Japanese patent application)
  • Patent Literature 2 JP-A-2006-253109
  • Patent Literature 3 JP-A-2008-112620
  • Patent Literature 4 JP-B-55-45626 (“JP-B” means examined Japanese patent publication)
  • the present invention is contemplated for providing an aluminum alloy conductor, which has sufficient electrical conductivity and tensile strength, and which is excellent in resistance to bending fatigue, flexibility, and the like.
  • the inventors of the present invention having studied keenly, found that an aluminum alloy conductor, which has excellent resistance to bending fatigue, mechanical strength, flexibility, and electrical conductivity, can be produced, by controlling the particle sizes and area ratios of two kinds of intermetallic compounds in an aluminum alloy to which specific additive elements are added, by controlling production conditions, such as a cooling speed in casting, and those in an intermediate annealing and a finish annealing.
  • the present invention is attained based on those findings.
  • An aluminum alloy conductor containing: 0.4 to 0.9 mass % of Fe, with the balance being Al and inevitable impurities,
  • the conductor contains two kinds of intermetallic compounds A and B, in which
  • the intermetallic compound A has a particle size within the range of 0.1 ⁇ m or more but 2 ⁇ m or less,
  • the intermetallic compound B has a particle size within the range of 0.03 ⁇ m or more but less than 0.1 ⁇ m, and
  • an area ratio a of the intermetallic compound A, and an area ratio b of the intermetallic compound B, in an arbitrary region in the conductor, satisfy the relationships of 1% ⁇ a ⁇ 6%, and 1% ⁇ b ⁇ 5%, respectively.
  • An aluminum alloy conductor containing: 0.4 to 0.9 mass % of Fe, and 0.01 to 0.4 mass % of Zr, with the balance being Al and inevitable impurities,
  • the conductor contains two kinds of intermetallic compounds A and B, in which
  • the intermetallic compound A has a particle size within the range of 0.1 ⁇ m or more but 2 ⁇ m or less,
  • the intermetallic compound B has a particle size within the range of 0.03 ⁇ m or more but less than 0.1 ⁇ m, and
  • an area ratio a of the intermetallic compound A, and an area ratio b of the intermetallic compound B, in an arbitrary region in the conductor, satisfy the relationships of 1% ⁇ a ⁇ 6%, and 1% ⁇ b ⁇ 7.5%, respectively.
  • the aluminum alloy conductor according to (1) or (2) which has a grain size at a vertical cross-section in the wire-drawing direction of 1 to 15 ⁇ m, by subjecting to a continuous electric heat treatment, which comprises the steps of rapid heating and quenching at the end of the production process of the conductor.
  • the aluminum alloy conductor according to any one of (1) to (3) which has a tensile strength of 80 MPa or more, and an electrical conductivity of 60% IACS or more.
  • the aluminum alloy conductor according to any one of (1) to (4) which has a tensile elongation at breakage of 10% or more.
  • the aluminum alloy conductor according to any one of (1) to (5) which has a recrystallized microstructure.
  • the aluminum alloy conductor of the present invention is excellent in the mechanical strength, the flexibility, and the electrical conductivity, and is useful as a conductor for a battery cable, a harness, or a motor, each of which is mounted on a movable body, and thus can also be preferably used for a door, a trunk, a hood (or a bonnet), and the like, for which an excellent resistance to bending fatigue is required.
  • FIG. 1 is an explanatory view of the test for measuring the number of times of repeated breakage, which was conducted in the Examples.
  • a preferable first embodiment of the present invention is an aluminum alloy conductor, which contains 0.4 to 0.9 mass % of Fe, with the balance being Al and inevitable impurities,
  • the conductor contains two kinds of intermetallic compounds A and B, in which
  • the intermetallic compound A has a particle size within the range of 0.1 ⁇ m or more but 2 ⁇ m or less,
  • the intermetallic compound B has a particle size within the range of 0.03 ⁇ m or more but less than 0.1 ⁇ m, and
  • the area ratio a of the intermetallic compound A, and the area ratio b of the intermetallic compound B, in an arbitrary region in the conductor satisfy the relationships of 1% ⁇ a ⁇ 6%, and 1% ⁇ b ⁇ 5%, respectively.
  • the reason why the content of Fe is set to 0.4 to 0.9 mass % is to utilize various effects by mainly Al—Fe-based intermetallic compounds.
  • Fe is made into a solid solution in aluminum in an amount of only 0.05 mass % at 655° C., and is made into a solid solution lesser at room temperature.
  • the remainder of Fe is crystallized or precipitated as intermetallic compounds, such as Al—Fe, and Al—Fe—Si.
  • the crystallized or precipitated product acts as a refiner for grains to make the grain size fine, and enhances the mechanical strength and resistance to bending fatigue.
  • the content of Fe is preferably 0.4 to 0.8 mass %, more preferably 0.5 to 0.7 mass %.
  • a preferable second embodiment of the present invention is an aluminum alloy conductor, which contains 0.4 to 0.9 mass % of Fe, and 0.01 to 0.4 mass % of Zr, with the balance being Al and inevitable impurities.
  • the conductor contains two kinds of intermetallic compounds A and B, in which
  • the intermetallic compound A has a particle size within the range of 0.1 ⁇ m or more but 2 ⁇ m or less,
  • the intermetallic compound B has a particle size within the range of 0.03 ⁇ m or more but less than 0.1 ⁇ m, and
  • the area ratio a of the intermetallic compound A, and the area ratio b of the intermetallic compound B, in an arbitrary region in the conductor satisfy the relationships of 1% ⁇ a ⁇ 6%, and 1% ⁇ b ⁇ 7.5%, respectively.
  • the alloy composition is that 0.01 to 0.4 mass % of Zn is further contained, in addition to the alloy composition of the above-mentioned first embodiment.
  • Zr forms an intermetallic compound with Al, and is made into a solid solution in Al, thereby to contribute to enhancement in mechanical strength and improvement in heat resistance of the aluminum alloy conductor.
  • the content of Zr is preferably 0.1 to 0.35 mass %, more preferably 0.15 to 0.3 mass %.
  • an aluminum alloy conductor of the present invention by defining the sizes (particle sizes) and area ratios of the intermetallic compounds, besides the above-mentioned alloying elements, an aluminum alloy conductor can be obtained, which has the desired excellent resistance to bending fatigue, mechanical strength, flexibility, and electrical conductivity.
  • the present invention contains two kinds of intermetallic compounds different in particle size each other at the respective predetermined area ratios.
  • the intermetallic compounds are particles of crystallized products, precipitated products, and the like, which are present inside the grains.
  • the crystallized products are formed upon melt-casting, and the precipitated products are formed in intermediate annealing and finish annealing, such as particles of Al—Fe, Al—Fe—Si, and Al—Zr.
  • the area ratio refers to the ratio of the intermetallic compound contained in the present alloy as represented in terms of area, and can be calculated as mentioned in detail below, based on a picture observed by TEM.
  • the intermetallic compound A is mainly constituted by Al—Fe, and is partially composed of Al—Fe—Si, Al—Zr, and the like. These intermetallic compounds act as refiners for grains, and enhance the mechanical strength and resistance to bending fatigue.
  • the reason why the area ratio a of the intermetallic compound A is set to 1% ⁇ a ⁇ 6% is that, when the area ratio is too small, these effects are insufficient. When the area ratio is too large, wire breaking is apt to occur due to the intermetallic compound. Furthermore, the intended resistance to bending fatigue cannot be obtained, and the flexibility is also lowered.
  • the intermetallic compound B is mainly constituted by Al—Fe—Si, Al—Zr, and the like. These intermetallic compounds enhance the mechanical strength and improve resistance to bending fatigue, through precipitation.
  • the reason why the area ratio b of the intermetallic compound B is set to 1% ⁇ b ⁇ 5% in the first embodiment and 1% ⁇ b ⁇ 7.5% in the second embodiment is that, when the area ratio is too small, these effects are insufficient, and when the area ratio is too large, it becomes a cause of wire breakage due to excess precipitation. Furthermore, the flexibility is also lowered.
  • the area ratios of the intermetallic compounds A and B of two kinds of sizes to the above-mentioned values, it is necessary to set the respective alloy compositions to the above-mentioned ranges.
  • the area ratios can be realized by suitably controlling the cooling speed in casting, the intermediate annealing temperature, the conditions in finish annealing, and the like.
  • the cooling speed in casting refers to an average cooling speed from the initiation of solidification of an aluminum alloy ingot to 200° C.
  • the following three methods may be exemplified. Namely, (1) changing the size (wall thickness) of an iron casting mold, (2) forcedly-cooling by disposing a water-cooling mold on the bottom face of a casting mold (the cooling speed is changed also by changing the amount of water), and (3) changing the casting amount of a molten metal.
  • the cooling speed in casting is too slow, the crystallized product of the Al—Fe system is coarsened and thus the intended microstructure cannot be obtained, which results in being apt to occur cracking.
  • the cooling speed in casting is preferably 1 to 20° C./sec, more preferably 5 to 15° C./sec.
  • the intermediate annealing temperature refers to a temperature when a heat treatment is conducted in the mid way of wire drawing.
  • the intermediate annealing is mainly conducted for recovering the flexibility of a wire that has been hardened by wire drawing.
  • the intermediate annealing temperature is too low, recrystallization is insufficient and thus the yield strength is excessive and the flexibility cannot be ensured, which result in a high possibility that wire breakage may occur in the later wire drawing and a wire cannot be obtained.
  • the resultant wire is in an excessively annealed state, and the recrystallized grains become coarse and thus the flexibility is significantly lowered, which result in a high possibility that wire breakage may occur in the later wire drawing and a wire cannot be obtained.
  • the intermediate annealing temperature is generally 300 to 450° C., preferably 350 to 450° C.
  • the time period for intermediate annealing is generally 30 min or more. If the time period is less than 30 min, the time period required for the formation and growth of recrystallized grains is insufficient, and thus the flexibility of the wire cannot be recovered.
  • the time period is preferably 1 to 6 hours.
  • the average cooling speed from the heat treatment temperature in the intermediate annealing to 100° C. is not particularly defined, it is desirably 0.1 to 10° C./min.
  • the finish annealing is conducted, for example, by a continuous electric heat treatment in which annealing is conducted by the Joule heat generated from the wire in interest itself that is running continuously through two electrode rings, by passing an electrical current through the wire.
  • the continuous electric heat treatment has the steps of: rapid heating and quenching, and can conduct annealing of the wire, by controlling the temperature of the wire and the time period.
  • the cooling is conducted, after the rapid heating, by continuously passing the wire through water. In one of or both of the case where the wire temperature in annealing is too low or too high and the case where the annealing time period is too short or too long, an intended microstructure cannot be obtained.
  • the flexibility that is required for attaching the resultant wire to vehicle to mount thereon cannot be obtained; and in one of or both of the case where the wire temperature in annealing is too high and in the case where the annealing time period is too long, the mechanical strength is lowered and the resistance to bending fatigue also becomes worse.
  • the wire temperature represents the highest temperature of the wire at immediately before passing through water.
  • the finish annealing may be, for example, a continuous annealing in which annealing is conducted by continuously passing the wire in an annealing furnace kept at a high temperature, or an induction heating in which annealing is conducted by continuously passing the wire in a magnetic field, each of which has the steps of rapid heating and quenching.
  • the annealing conditions are not identical with the conditions in the continuous electric heat treatment, since the atmospheres and heat-transfer coefficients are different from each other, even in the cases of these continuous annealing and induction heating each of which has the steps of rapid heating and quenching, the aluminum alloy conductor of the present invention can be prepared, by suitably controlling the finish-annealing conditions (thermal history) by referring to the annealing conditions in the continuous electric heat treatment as a typical example, so that the aluminum alloy conductor of the present invention having a prescribed precipitation state of the intermetallic compounds can be obtained.
  • the aluminum alloy conductor of the present invention has a grain size of 1 to 15 ⁇ m in a vertical cross-section in the wire-drawing direction. This is because, when the grain size is too small, a partial recrystallized microstructure remains and the tensile elongation at breakage is lowered conspicuously, and on the other hand, when too large, a coarse microstructure is formed and deformation behavior becomes uneven, and the tensile elongation at breakage is lowered similar to the above, and further the strength is lowered conspicuously.
  • the grain size is more preferably 1 to 10 ⁇ m.
  • the aluminum alloy conductor of the present invention preferably has a tensile strength (TS) of 80 MPa or more and an electrical conductivity of 60% IACS or more, preferably has a tensile strength of 80 to 150 MPa and an electrical conductivity of 60 to 65% IACS, more preferably has a tensile strength of 100 to 140 MPa and an electrical conductivity of 61 to 64% IACS.
  • TS tensile strength
  • the tensile strength and the electrical conductivity are conflicting properties, and the higher the tensile strength is, the lower the electrical conductivity is, whereas pure aluminum low in tensile strength is high in electrical conductivity. Therefore, in the case where an aluminum alloy conductor has a tensile strength of less than 80 MPa, the mechanical strength, including that in handling thereof, is low, and thus the conductor is difficult to be used as an industrial conductor. It is preferable that the electrical conductivity is 60% IACS or more, since a high current of dozens of amperes (A) is to pass through it when the conductor is used as a power line.
  • the aluminum alloy conductor of the present invention has sufficient flexibility. This can be obtained by conducting the above-mentioned finish annealing.
  • a tensile elongation at breakage is used as an index of flexibility of the aluminum alloy conductor, and is preferably 10% or more. This is because if the tensile elongation at breakage is too small, wire-running (i.e. an operation of attaching of it to a vehicle body) in installation of an electrical wiring becomes difficult as mentioned above. Furthermore, if the tensile elongation at breakage is too high, the mechanical strength becomes insufficient and the resultant conductor is weak in wire-running, which may results in wire breakage.
  • the tensile elongation at breakage is more preferably 20% to 50%, further preferably 25 to 45%.
  • the aluminum alloy conductor of the present invention can be produced via steps of: [1] melting, [2] casting, [3] hot- or cold-working (e.g. caliber rolling with grooved rolls), [4] wire drawing, [5] heat treatment (intermediate annealing), [6] wire drawing, and [7] heat treatment (finish annealing).
  • Fe and Al, or Fe, Zr, and Al are melted at amounts that provide the desired contents.
  • a molten metal is rolled while the molten metal is continuously cast in a water-cooled casting mold; by using a Properzi-type continuous cast-rolling machine which has a casting ring and a belt in combination, to give a rod of about 10 mm in diameter.
  • the cooling speed in casting at this time is generally 1 to 20° C./sec as mentioned above.
  • the casting and hot rolling may be conducted by billet casting at a cooling speed in casting of 1 to 20° C./sec, extrusion, or the like.
  • the wire drawing becomes difficult due to excess work-hardening, which is problematic in the quality in that, for example, wire breakage occurs upon the wire drawing.
  • the surface of the wire is cleaned up by conducting peeling of the surface thereof, the peeling may be omitted.
  • the thus-worked product that has undergone cold drawing i.e. a roughly-drawn wire
  • the conditions for the intermediate annealing are generally 300 to 450° C. and 30 minutes or more.
  • the thus-annealed roughly-drawn wire is further subjected to wire drawing.
  • the working degree is desirably 1 or more but 6 or less for the above-mentioned reasons.
  • the thus-cold-drawn wire is subjected to finish annealing by the continuous electric heat treatment. It is preferable that the conditions for the annealing satisfy: 26x ⁇ 0.6 +377 ⁇ y ⁇ 19x ⁇ 0.6 +477, in the range of 0.03 ⁇ x ⁇ 0.55, when the numerical formula represented by the wire temperature y (° C.) and the annealing time period x (sec) are used as mentioned above.
  • the aluminum alloy conductor of the present invention that is prepared by the heat treatment as mentioned above has a recrystallized microstructure.
  • the recrystallized microstructure refers to a state of a microstructure that is constituted by grains that have little lattice defects, such as dislocation, introduced by plastic working. Since the conductor has a recrystallized microstructure, the tensile elongation at breakage and electrical conductivity are recovered, and a sufficient flexibility can be obtained.
  • Fe and Al, or Fe, Zr, and Al in the amounts shown in Table 1-1 and Table 2-1 (mass %) were rolled by using a Properzi-type continuous cast-rolling machine while the molten metal was continuously cast in a water-cooled casting mold, to give respective rod materials with diameter about 10 mm. At that time, the cooling speed in casting was 1 to 20° C./sec (in Comparative Examples, the cases of 0.2° C./sec or 50° C./sec were also included).
  • a continuous electric heat treatment as the finish annealing was conducted at a temperature of 461 to 621° C. (in Comparative Examples, the cases of 432° C., 435° C., 450° C., 460° C., or 623° C. were also included) for a time period of 0.03 to 0.54 second.
  • the temperature was measured at immediately above the water surface where the temperature of the wire would be the highest, with a fiber-type radiation thermometer (manufactured by Japan Sensor Corporation).
  • the conditions of the electrolytic polishing were as follows: polish liquid, a 20% ethanol solution of perchloric acid; liquid temperature, 0 to 5° C.; voltage, 10 V; current, 10 mA; and time period, 30 to 60 seconds. Then, in order to obtain a contrast of grains, the resultant sample was subjected to anodizing finishing, with 2% hydrofluoroboric acid, under conditions of voltage 20 V, electrical current 20 mA, and time period 2 to 3 min.
  • the resultant microstructure was observed by an optical microscope with a magnification of 200 ⁇ to 400 ⁇ and photographed, and the grain size was measured by an intersection method. Specifically, a straight line was drawn arbitrarily on a microscopic picture taken, and the number of intersection points at which the length of the straight line intersected with the grain boundaries was measured, to determine an average grain size. The grain size was evaluated by changing the length and the number of straight lines so that 50 to 100 grains would be counted.
  • the wires of Examples and Comparative Examples were each formed into a thin film by an electropolishing thin-film method (twin-jet polishing), and an arbitrary region was observed with a magnification of 6,000 ⁇ to 30,000 ⁇ , by using a transmission electron microscope (TEM). Then, electron beam was focused on the intermetallic compounds by using an energy-dispersive X-ray detector (EDX), thereby to detect intermetallic compounds of an Al—Fe-based, an Al—Fe—Si-based, and an Al—Zr-based.
  • EDX energy-dispersive X-ray detector
  • the sizes of the intermetallic compounds were each judged from the scale of the picture taken, which were calculated by converting the shape of the individual particle to the sphere which was equal to the volume of the individual particle.
  • the area ratios a and b of the intermetallic compounds were obtained, based on the picture taken, by setting a region in which about 5 to 10 particles would be counted for the intermetallic compound A, and a region in which 20 to 50 particles would be counted for the intermetallic compound B, calculating the areas of the intermetallic compounds from the sizes and the numbers of respective intermetallic compounds, and dividing the areas of the respective intermetallic compounds by the areas of the regions for the counting.
  • the area ratios were each calculated, by using a reference thickness of 0.15 ⁇ m for the thickness of a slice of the respective sample.
  • the area ratio was able to be calculated, by converting the sample thickness to the reference thickness, i.e. by multiplying the area ratio calculated based on the picture taken by (reference thickness/sample thickness).
  • the sample thickness was calculated by observing the interval of equal thickness fringes observed on the picture, and was approximately 0.15 ⁇ m in all of the samples.
  • a strain amplitude at an ordinary temperature was set to ⁇ 0.17%.
  • the resistance to bending fatigue varies depending on the strain amplitude.
  • the strain amplitude can be determined by the wire diameter of a wire 1 and the curvature radii of bending jigs 2 and 3 as shown in FIG. 1 , a bending fatigue test can be conducted by arbitrarily setting the wire diameter of the wire 1 and the curvature radii of the bending jigs 2 and 3 .
  • One end of the wire was fixed on a holding jig 5 so that bending can be conducted repeatedly, and a weight 4 of about 10 g was hanged from the other end. Since the holding jig 5 moves in the test, the wire 1 fixed thereon also moves, thereby repeating bending can be conducted. The repeating was conducted under the condition of 1.5 Hz (1.5 times of reciprocation in 1 second), and the test machine has a mechanism in which the weight 4 falls to stop counting when the test piece of the wire 1 is broken.
  • the number of openings and closings is 36,500 (calculated by regarding 1 year to be 365 days). Since an electrical wire which is actually used is not a single wire but in a twisted wire structure, and is subjected to a coating treatment, the load on the electrical wire conductor becomes as less as one severalth.
  • the number of repeating times at breakage is preferably 50,000 or more, more preferably 70,000 or more, by which sufficient resistance to bending fatigue can be ensured as an evaluation value in a single wire.
  • Comparative Examples 101 to 103 the alloying elements added to the aluminum alloy were outside of the ranges according to the present invention.
  • Comparative Example 101 since the content of Fe was too low, the ratios of the intermetallic compounds A and B were too low, and the tensile strength and the number of repeating times at breakage were poor.
  • Comparative Example 102 since the content of Fe was too large, the ratios of the intermetallic compounds A and B were too large, and the number of repeating times at breakage and the electrical conductivity were poor.
  • Comparative Example 103 since the content of Zr was too large, the ratio of the intermetallic compound B was too large, and the number of repeating times at breakage and the electrical conductivity were poor.
  • Comparative Examples 104 to 110, and 201 show the cases where the area ratios of the intermetallic compounds in the respective aluminum alloy conductor were outside of the ranges according to the present invention, or the cases where the conductors were broken in the course of production. Those Comparative Examples show that no aluminum alloy conductor as defined in the present invention was able to be obtained, depending on the conditions for the production of the aluminum alloy.
  • Comparative Example 104 since the cooling speed in casting was too slow, the target conductor wire was broken in the wire drawing step.
  • Comparative Example 105 since the cooling speed in casting was too fast, the ratio of the intermetallic compound A was too low and the ratio of the intermetallic compound B was too large, and the number of repeating times at breakage and the electrical conductivity were poor.
  • Comparative Examples 106 to 108 since the temperature for the intermediate annealing was too high or low or the time period for the intermediate annealing was too short, the target conductor wires were broken in the wire drawing step.
  • Comparative Example 109 since the resultant alloy was in an unannealed state due to insufficient softening in the finish-annealing step and no intermetallic compound was observed, the tensile elongation at breakage was poor.
  • Comparative Example 110 since the ratio of the intermetallic compound B was too low due to a too high temperature for the finish annealing, the tensile strength, the electrical conductivity, the tensile elongation at breakage, and the number of repeating times at breakage were poor.
  • Comparative Example 201 in which the finish annealing was conducted by using a batch-type annealing furnace, since the ratio of the intermetallic compound B was too low, the number of repeating times at breakage was poor.
  • the aluminum alloy conductors were able to be obtained, which were excellent in the tensile strength, the electrical conductivity, the tensile elongation at breakage (the flexibility), and the number of repeating times at breakage (the resistance to bending fatigue).

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US13/594,480 2010-02-26 2012-08-24 Aluminum alloy conductor Abandoned US20120321507A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2010-043489 2010-02-26
JP2010043489 2010-02-26
PCT/JP2011/054399 WO2011105586A1 (ja) 2010-02-26 2011-02-25 アルミニウム合金導体

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CN102803531A (zh) 2012-11-28
WO2011105586A1 (ja) 2011-09-01
EP2540850A1 (de) 2013-01-02
JPWO2011105586A1 (ja) 2013-06-20
JP4986253B2 (ja) 2012-07-25
CN102803531B (zh) 2015-11-25
EP2540850B1 (de) 2017-11-15
EP2540850A4 (de) 2013-11-06

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