WO2011105586A1 - Aluminum alloy conductor - Google Patents

Aluminum alloy conductor Download PDF

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Publication number
WO2011105586A1
WO2011105586A1 PCT/JP2011/054399 JP2011054399W WO2011105586A1 WO 2011105586 A1 WO2011105586 A1 WO 2011105586A1 JP 2011054399 W JP2011054399 W JP 2011054399W WO 2011105586 A1 WO2011105586 A1 WO 2011105586A1
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WIPO (PCT)
Prior art keywords
aluminum alloy
conductor
intermetallic compound
alloy conductor
wire
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PCT/JP2011/054399
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French (fr)
Japanese (ja)
Inventor
茂樹 関谷
京太 須齋
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古河電気工業株式会社
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Application filed by 古河電気工業株式会社 filed Critical 古河電気工業株式会社
Priority to JP2011528135A priority Critical patent/JP4986253B2/en
Priority to EP11747542.6A priority patent/EP2540850B1/en
Priority to CN201180010674.4A priority patent/CN102803531B/en
Publication of WO2011105586A1 publication Critical patent/WO2011105586A1/en
Priority to US13/594,480 priority 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 used as a conductor of an electric wiring body.
  • the cross-sectional area of a pure aluminum conductor needs to be about 1.5 times that of a pure copper conductor, but the weight is still about half that of copper. is there.
  • the above% IACS represents the electrical conductivity when the resistivity 1.7241 ⁇ 10 ⁇ 8 ⁇ m of universal standard annealed copper (International Annealed Copper Standard) is 100% IACS.
  • a material having higher strength has better fatigue characteristics. Therefore, a high-strength aluminum conductor may be applied.
  • the wire harness is required to be easily handled (installation work on the vehicle body) at the time of installation, in general, flexibility can be secured.
  • Dull material annealed material is often used.
  • the aluminum conductor used for the electric wiring body of the moving body has excellent bending fatigue resistance in addition to the strength and flexibility required for handling and mounting, and the conductivity required to flow a lot of electricity. Materials are needed.
  • pure aluminum systems such as aluminum alloy wire rods for power transmission lines (JIS A1060 and JIS A1070) cannot sufficiently withstand repeated bending stresses that occur when doors are opened and closed.
  • alloying with various additive elements is excellent in strength, it causes a decrease in electrical conductivity due to the solid solution phenomenon of the additive elements in aluminum, decreases flexibility, and excessive metals in aluminum. It was a problem that a wire breakage caused by an intermetallic compound occurred during wire drawing by forming an intermetallic compound. Therefore, it is essential to limit and select the additive element and not to disconnect, to prevent a decrease in conductivity and a decrease in flexibility, and to improve strength and bending fatigue resistance.
  • Patent Document 1 Representative examples of aluminum conductors used for electric wiring bodies of moving bodies include those described in Patent Documents 1 to 4.
  • the inventions described in any of the patent documents have further problems to be solved. Since the invention of Patent Document 1 does not perform finish annealing, it cannot secure the flexibility required for the mounting work on the vehicle body.
  • the invention of Patent Document 2 discloses finish annealing, and the conditions are such that the intermetallic compound can be controlled so as to improve the bending fatigue resistance and conductivity while maintaining excellent flexibility. Is different.
  • the invention of Patent Document 3 since the amounts of Mg and Si are large, the intermetallic compound cannot be appropriately controlled, which causes disconnection during wire drawing.
  • the invention of Patent Document 4 is a technique that is being replaced with an alternative product from the viewpoint of environmental load because it contains antimony (Sb) as an additive element.
  • Sb antimony
  • An object of the present invention is to provide an aluminum alloy conductor having sufficient electrical conductivity and tensile strength, and excellent in bending fatigue resistance, flexibility and the like.
  • the inventors of the present invention have made various studies, and by controlling the production conditions such as casting cooling rate, intermediate annealing, and finish annealing for the aluminum alloy to which a specific additive element is added, the particle size and area of two kinds of intermetallic compounds. It has been found that an aluminum alloy conductor having excellent bending fatigue resistance, strength, flexibility and electrical conductivity can be produced by controlling the rate, and the present invention has been completed based on this finding.
  • the present invention provides the following solutions.
  • Two types of intermetallic compounds A and B exist in the conductor The particle size of the intermetallic compound A is in the range of 0.1 ⁇ m to 2 ⁇ m, The particle size of the intermetallic compound B is in the range of 0.03 ⁇ m or more and less than 0.1 ⁇ m,
  • the area ratio a of the intermetallic compound A and the area ratio b of the intermetallic compound B in an arbitrary range in the conductor satisfy 1% ⁇ a ⁇ 6% and 1% ⁇ b ⁇ 5%, respectively.
  • Aluminum alloy conductor characterized by (2) An aluminum alloy conductor containing 0.4 to 0.9 mass% of Fe and 0.01 to 0.4 mass% of Zr, the balance being Al and inevitable impurities, Two types of intermetallic compounds A and B exist in the conductor, The particle size of the intermetallic compound A is in the range of 0.1 ⁇ m to 2 ⁇ m, The particle size of the intermetallic compound B is in the range of 0.03 ⁇ m or more and less than 0.1 ⁇ m, The area ratio a of the intermetallic compound A and the area ratio b of the intermetallic compound B in an arbitrary range in the conductor satisfy 1% ⁇ a ⁇ 6% and 1% ⁇ b ⁇ 7.5%, respectively.
  • An aluminum alloy conductor characterized by: (3) A continuous energization heat treatment including a rapid heating and rapid cooling process is performed at the end of the manufacturing process of the conductor, so that the crystal grain size in the vertical cross section in the wire drawing direction is 1 to 15 ⁇ m (1) or The aluminum alloy conductor according to (2). (4) The aluminum alloy conductor according to any one of (1) to (3), wherein the tensile strength is 80 MPa or more and the electrical conductivity is 60% IACS or more. (5) The aluminum alloy conductor according to any one of (1) to (4), which has a tensile elongation at break of 10% or more. (6) The aluminum alloy conductor according to any one of (1) to (5), which has a recrystallized structure.
  • the aluminum alloy conductor of the present invention is excellent in strength, flexibility and electrical conductivity, and is useful as a battery cable, harness or motor conductor mounted on a moving body, doors and trunks that require excellent bending fatigue resistance, It can be suitably used for a bonnet or the like.
  • a preferred first embodiment of the present invention is an aluminum alloy conductor containing 0.4 to 0.9 mass% of Fe and comprising the balance Al and inevitable impurities,
  • Two types of intermetallic compounds A and B exist in the conductor The particle size of the intermetallic compound A is in the range of 0.1 ⁇ m to 2 ⁇ m, The particle size of the intermetallic compound B is in the range of 0.03 ⁇ m or more and less than 0.1 ⁇ m,
  • the area ratio a of the intermetallic compound A and the area ratio b of the intermetallic compound B in an arbitrary range in the conductor satisfy 1% ⁇ a ⁇ 6% and 1% ⁇ b ⁇ 5%, respectively.
  • the reason why the Fe content is set to 0.4 to 0.9 mass% is mainly to use various effects of the Al—Fe-based intermetallic compound. Fe dissolves only 0.05 mass% in aluminum at 655 ° C., and is even less at room temperature. The remainder crystallizes or precipitates as an intermetallic compound such as Al—Fe or Al—Fe—Si. This crystallized product or precipitate acts as a crystal grain refining material, and improves strength and bending fatigue resistance. If the Fe content is too small, these effects are insufficient, and if it is too much, the crystallized material becomes coarse and the wire drawing workability is poor, the desired bending fatigue resistance cannot be obtained, and the flexibility also decreases. . Moreover, it will be in a supersaturated solid solution state and electrical conductivity will also fall.
  • the Fe content is preferably 0.4 to 0.8 mass%, more preferably 0.5 to 0.7 mass%.
  • a preferred second embodiment of the present invention is an aluminum alloy conductor containing 0.4 to 0.9 mass% Fe and 0.01 to 0.4 mass% Zr, and the balance being Al and inevitable impurities.
  • Two types of intermetallic compounds A and B exist in the conductor The particle size of the intermetallic compound A is 0.1 ⁇ m or more and 2 ⁇ m or less, The particle size of the intermetallic compound B is 0.03 ⁇ m or more and less than 0.1 ⁇ m, The area ratio a of the intermetallic compound A and the area ratio b of the intermetallic compound B satisfy 1% ⁇ a ⁇ 6% and 1% ⁇ b ⁇ 7.5%.
  • the alloy composition includes 0.01 to 0.4 mass% of Zr in addition to the alloy composition of the first embodiment described above.
  • Zr forms an intermetallic compound with Al, and forms a solid solution in Al, thereby contributing to the improvement of the strength and heat resistance of the aluminum alloy conductor. If the Zr content is too small, the effect cannot be expected. If the Zr content is too large, the melting temperature becomes high and it becomes difficult to form a drawn wire. In addition, the conductivity and flexibility are lowered, and the bending fatigue resistance is also deteriorated.
  • the Zr content is preferably 0.1 to 0.35 mass%, more preferably 0.15 to 0.3 mass%.
  • Other alloy compositions and their actions are the same as in the first embodiment described above.
  • the aluminum alloy conductor of the present invention has desired excellent bending fatigue resistance, strength, flexibility and electrical conductivity by defining the size (particle diameter) and area ratio of the intermetallic compound. An aluminum alloy conductor can be obtained.
  • the present invention contains two kinds of intermetallic compounds having different particle diameters at a predetermined area ratio.
  • an intermetallic compound is particles, such as a crystallized substance and a precipitate, which exist in crystal grains.
  • the crystallized material is mainly formed during melt casting, and the precipitate is formed by intermediate annealing and finish annealing, for example, particles such as Al—Fe, Al—Fe—Si, and Al—Zr.
  • the area ratio represents the ratio of intermetallic compounds contained in the present alloy in terms of area, and can be calculated as described in detail below based on a photograph observed by TEM.
  • the intermetallic compound A is mainly composed of Al—Fe, and a part thereof includes Al—Fe—Si, Al—Zr and the like. These intermetallic compounds work as crystal grain refiners and improve strength and bending fatigue resistance.
  • the reason why the area ratio a of the intermetallic compound A is 1% ⁇ a ⁇ 6% is that these effects are insufficient if the amount is too small, and if the amount is too large, disconnection is likely to occur due to the intermetallic compound. Flexural fatigue characteristics cannot be obtained and flexibility is also reduced.
  • the intermetallic compound B is mainly composed of Al—Fe—Si and Al—Zr. These intermetallic compounds improve strength and bending fatigue resistance by precipitation.
  • 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. This is because it is insufficient, and if it is too much, it causes disconnection due to excessive precipitation. Also, flexibility is reduced.
  • the intermetallic compounds A and B having two types of dimensions in order to set the area ratio to the above value, it is necessary to set each alloy composition within the above-described range. is there. And it is realizable by controlling appropriately a casting cooling rate, intermediate annealing temperature, finish annealing conditions, etc.
  • the casting cooling rate is an average cooling rate from the start of solidification of the aluminum alloy ingot to 200 ° C.
  • a method for changing the cooling rate for example, the following three methods can be cited. That is, (1) change the size (thickness) of the iron mold, (2) provide a water cooling mold on the lower surface of the mold and forcibly cool (the cooling speed also changes by changing the amount of water), (3) the amount of molten metal cast Change. If the casting cooling rate is too slow, the Al—Fe-based crystallized product becomes coarse, and the desired structure cannot be obtained, and cracking tends to occur. If it is too fast, an excessive solid solution of Fe occurs, the target structure cannot be obtained, and the electrical conductivity is lowered. In some cases, casting cracks can also occur.
  • the casting cooling rate is usually 1 to 20 ° C./second, preferably 5 to 15 ° C./second.
  • the intermediate annealing temperature is the temperature at which heat treatment is performed during wire drawing.
  • the intermediate annealing is performed mainly to regain the flexibility of the wire that has been hardened by wire drawing. If the intermediate annealing temperature is too low, the recrystallization is insufficient and the yield strength becomes excessive, so that flexibility cannot be secured, and there is a high possibility that the wire will not be obtained due to the subsequent wire drawing. When too high, it will be in an over-annealed state, recrystallization grain coarsening will occur and flexibility will fall remarkably, and the possibility that a wire will not be obtained due to breakage in the subsequent wire drawing will increase.
  • the intermediate annealing temperature is usually 300 to 450 ° C, preferably 350 to 450 ° C.
  • the time for the intermediate annealing is usually 30 minutes or more. This is because if it is less than 30 minutes, the time required for the formation and growth of recrystallized grains is insufficient, and the flexibility of the wire cannot be recovered. Preferably it is 1 to 6 hours.
  • the average cooling rate from the heat treatment temperature during intermediate annealing to 100 ° C. is not particularly specified, but is preferably 0.1 to 10 ° C./min.
  • the finish annealing is performed, for example, by continuous energization heat treatment in which annealing is performed by Joule heat generated from itself by passing an electric current through a wire that passes through two electrode wheels.
  • the continuous energization heat treatment includes rapid heating and rapid cooling steps, and can be annealed by controlling the wire temperature and time. Cooling is performed by passing the wire continuously through water after rapid heating. If the wire temperature during annealing is too low or too high, or if one or both of the annealing times are too short or too long, the desired structure cannot be obtained.
  • the wire temperature during annealing is too low, if one or both of the annealing time is too short, the necessary flexibility when mounting on the vehicle is not obtained, if the wire temperature during annealing is too high, In one or both of cases where the annealing time is too long, the strength is lowered and the bending fatigue resistance is also deteriorated. That is, the wire temperature y (° C.), the use of equations represented by annealing time x (seconds), 26x -0.6 + 377 within a range of 0.03 ⁇ x ⁇ 0.55 ⁇ y ⁇ 19x -0.6 It is necessary that the annealing conditions satisfy +477.
  • the wire temperature represents the temperature immediately before passing through the water, which is the highest in the wire.
  • finish annealing includes rapid heating and quenching processes in addition to continuous energization heat treatment, for example, running annealing in which the wire continuously anneals through an annealing furnace maintained at a high temperature, and the wire in the magnetic field. It may be induction heating that passes and anneals continuously.
  • the annealing conditions are not the same as those for continuous energization heat treatment because the atmosphere and heat transfer coefficient are different, but even in the case of running annealing and induction heating, including these rapid heating and quenching processes, the prescribed intermetallic compound
  • finish annealing conditions thermal history
  • the aluminum alloy conductor of the present invention having a precipitation state can be obtained.
  • the crystal grain size in the vertical cross section of the aluminum alloy conductor in the wire drawing direction is 1 to 15 ⁇ m.
  • the reason for this is that if the particle size is too small, the partially recrystallized structure remains and the tensile elongation at break is remarkably reduced, and if it is too large, a coarse structure is formed and the deformation behavior becomes non-uniform, and similarly the tensile break This is because the elongation is lowered and the strength is significantly lowered.
  • the crystal grain size is preferably 1 to 10 ⁇ m.
  • the aluminum alloy conductor of the present invention has a tensile strength (TS) of 80 MPa or more and a conductivity of 60% IACS or more, preferably a tensile strength of 80 to 150 MPa and a conductivity of 60 to 65% IACS, more preferably tensile.
  • the strength is 100 to 140 MPa and the conductivity is 61 to 64% IACS.
  • Tensile strength and electrical conductivity have contradictory properties. The higher the tensile strength, the lower the electrical conductivity, and conversely, pure aluminum with a low tensile strength has a higher electrical conductivity.
  • the conductivity is desirably 60% IACS or more.
  • the aluminum alloy conductor of the present invention has sufficient flexibility. This can be obtained by performing the above-described finish annealing.
  • the tensile elongation at break is used as an index of the flexibility of the aluminum alloy conductor, preferably 10% or more. The reason for this is that if the tensile elongation at break is too small, it becomes difficult to handle the wiring (for example, mounting work on the vehicle body) as described above. This is because it may cause The tensile elongation at break is more preferably 20 to 50%, still more preferably 25 to 45%.
  • the aluminum alloy conductor of the present invention includes [1] melting, [2] casting, [3] hot or cold processing (groove roll processing, etc.), [4] wire drawing, [5] heat treatment (intermediate annealing), It can be manufactured through steps of [6] wire drawing and [7] heat treatment (finish annealing).
  • the aluminum alloy conductor of the present invention produced by heat treatment as described above has a recrystallized structure.
  • the recrystallized structure is a structure state composed of crystal grains with few lattice defects such as dislocations introduced by plastic working. By having a recrystallized structure, tensile elongation at break and electrical conductivity are recovered, and sufficient flexibility can be obtained.
  • (A) Crystal grain size The cross section of the specimen cut out perpendicular to the wire drawing direction was filled with resin, and after mechanical polishing, electrolytic polishing was performed.
  • the electrolytic polishing conditions are: an ethanol solution containing 20% perchloric acid, a liquid temperature of 0 to 5 ° C., a voltage of 10 V, a current of 10 mA, and a time of 30 to 60 seconds.
  • anodic finishing was performed using 2% borohydrofluoric acid under the conditions of a voltage of 20 V, a current of 20 mA, and a time of 2 to 3 minutes. This structure was photographed with an optical microscope of 200 to 400 times, and the particle size was measured by a crossing method.
  • an average particle size was obtained by arbitrarily drawing a straight line on the photographed photo, and measuring the number of intersections of the length of the straight line and the grain boundary. The particle size was evaluated by changing the length and number of lines so that 50 to 100 particles could be counted.
  • (B) Identification of intermetallic compound, dimensions (particle diameter), and area ratio The wires of Examples and Comparative Examples were made into thin films by an electrolytic polishing thin film method (twin jet polishing method), and a transmission electron microscope (TEM) was used. An arbitrary range was observed at a magnification of 6000 to 30000 times.
  • the area ratios a and b of the intermetallic compound are set based on the photographed images, and a range in which about 5 to 10 for the intermetallic compound A and 20 to 50 for the intermetallic compound B can be counted.
  • the area of the intermetallic compound was calculated from the size and number of each intermetallic compound, and the area of each intermetallic compound was divided by the area of the range to be counted.
  • the area ratio is calculated by using the sample thickness of the thin piece as a reference thickness of 0.15 ⁇ m. If the sample thickness is different from the reference thickness, convert the sample thickness to the reference thickness, that is, by multiplying the area ratio calculated based on the photographed (reference thickness / sample thickness) The area ratio can be calculated.
  • the sample thickness was calculated by observing the interval of the equal thickness stripes observed from the photograph, and was about 0.15 ⁇ m in all the samples.
  • C Tensile strength and tensile elongation at break Three pieces each were tested according to JIS Z 2241, and the average value was obtained.
  • D Conductivity In a constant temperature bath holding a test piece having a length of 300 mm at 20 ° C. ( ⁇ 0.5 ° C.), three specific resistances were measured using the four probe method, and the average conductivity was measured. Calculated. The distance between the terminals was 200 mm.
  • E Number of repeated fractures As a standard for bending fatigue resistance, the strain amplitude at room temperature was ⁇ 0.17%.
  • Bending fatigue resistance varies with strain amplitude.
  • the strain amplitude can be determined by the wire diameter of the wire rod 1 and the bending radii of the bending jigs 2 and 3 shown in FIG. 1, the wire diameter of the wire rod 1 and the bending radii of the bending jigs 2 and 3 are arbitrarily set and bent. It is possible to conduct a fatigue test. By using a double-bending bending fatigue tester manufactured by Fujii Seiki Co., Ltd.
  • the wire 1 was inserted with a gap of 1 mm between the bending jigs 2 and 3, and repeatedly moved in such a manner as to be along the jigs 2 and 3.
  • One end of the wire was fixed to a holding jig 5 so that it could be bent repeatedly, and a weight 4 of about 10 g was hung from the other end.
  • the wire 1 fixed to the holding jig 5 also moves and can be bent repeatedly.
  • the repetition is performed under the condition of 1.5 Hz (1.5 reciprocations per second), and when the wire specimen 1 breaks, the weight 4 falls and stops counting. If the number of times of opening and closing per day is 10 and the use for 10 years is assumed, the number of times of opening and closing is 36500 (calculated as 365 days a year).
  • the actually used electric wire is not a single wire but has a stranded wire structure, and since the coating process is performed, the burden on the electric wire conductor becomes a fraction.
  • the number of repeated fractures of 50000 times or more that can ensure sufficient bending fatigue resistance as an evaluation value for a single wire is preferred, and more preferably 70000 times or more.
  • Comparative Examples 101 to 103 the additive component of the aluminum alloy is outside the scope of the present invention.
  • Comparative Example 101 since Fe is too small, intermetallic compounds A and B are reduced, and the tensile strength and the number of repeated fractures are poor.
  • Comparative Example 102 since there is too much Fe, intermetallic compounds A and B increase, and the number of repeated fractures and electrical conductivity are poor.
  • Comparative Example 103 since there is too much Zr, the intermetallic compound B increases, and the number of repeated fractures and the electrical conductivity are poor.
  • Comparative Examples 104 to 110 and Comparative Example 201 show that the area ratio of the intermetallic compound in the aluminum alloy conductor is out of the range of the present invention or is broken during the production.
  • an example is shown in which the aluminum alloy conductor defined by the present invention is not obtained depending on the production conditions of the aluminum alloy.
  • the casting cooling rate was too slow, so the wire was broken during wire drawing.
  • the casting cooling rate is too fast, the amount of intermetallic compound A is small, the amount of intermetallic compound B is large, and the number of repeated fractures and the electrical conductivity are poor.
  • Comparative Examples 106 to 108 the temperature of the intermediate annealing was too high or too low, or the time was too short.
  • Comparative Example 109 is in an unannealed state due to insufficient softening in the final annealing step, and no intermetallic compound was observed, so that the tensile elongation at break was poor.
  • Comparative Example 110 since the finish annealing temperature was too high, the amount of intermetallic compound B was small, and the tensile strength, electrical conductivity, tensile elongation at break, and number of repeated fractures were poor.
  • finish annealing was performed in a batch annealing furnace, but the amount of intermetallic compound B was reduced and the number of repeated fractures was poor.
  • Examples 1 to 13 aluminum alloy conductors excellent in tensile strength, electrical conductivity, tensile breaking elongation (flexibility), and number of repeated breaking (flexural fatigue resistance) were obtained.

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Abstract

In order to provide an aluminum alloy conductor having sufficient electrical conductivity and tensile strength, and having excellent flexibility, resistance to fatigue from flexing, and the like, disclosed is the belowmentioned aluminum alloy conductor: an aluminum alloy conductor containing 0.4-0.9 mass% of Fe, the remainder comprising Al and unavoidable impurities, wherein two types of intermetallic compounds (A, B) are present in the aforementioned conductor, the grain size of compound A is between 0.1 μm and 2 μm inclusive, the grain size of compound B is at least 0.03 μm and less than 0.1 μm, and in any given range within the aforementioned conductor, the area ratio (a) of compound A and the area ratio (b) of compound B respectively satisfy 1% ≤ a ≤ 6% and 1% ≤ b ≤ 5%.

Description

アルミニウム合金導体Aluminum alloy conductor
　本発明は、電気配線体の導体として用いられるアルミニウム合金導体に関するものである。 The present invention relates to an aluminum alloy conductor used as a conductor of an electric wiring body.
　従来、自動車、電車、航空機等の移動体の電気配線体として、ワイヤーハーネスと呼ばれる銅または銅合金の導体を含む電線に銅または銅合金（例えば、黄銅）製の端子（コネクタ）を装着した部材が用いられていたが、近年の移動体の軽量化の中で、電気配線体の導体として、銅又は銅合金より軽量なアルミニウム又はアルミニウム合金を用いる検討が進められている。
　アルミニウムの比重は銅の約１／３、アルミニウムの導電率は銅の約２／３（純銅を１００％ＩＡＣＳの基準とした場合、純アルミニウムは約６６％ＩＡＣＳ）であり、純アルミニウムの導体に純銅の導体と同じ電流を流すためには、純アルミニウムの導体の断面積を純銅の導体の約１．５倍にする必要があるが、それでも重量では銅に比べて約半分と有利な点がある。
　なお、上記の％ＩＡＣＳとは、万国標準軟銅（Ｉｎｔｅｒｎａｔｉｏｎａｌ　Ａｎｎｅａｌｅｄ　Ｃｏｐｐｅｒ　Ｓｔａｎｄａｒｄ）の抵抗率１．７２４１×１０－８Ωｍを１００％ＩＡＣＳとした場合の導電率を表したものである。 2. Description of the Related Art Conventionally, a member in which a terminal (connector) made of copper or copper alloy (for example, brass) is attached to an electric wire including a copper or copper alloy conductor called a wire harness as an electric wiring body of a moving body such as an automobile, a train, and an aircraft However, in light of the recent weight savings of moving bodies, studies are underway to use aluminum or aluminum alloys that are lighter than copper or copper alloys as conductors of electrical wiring bodies.
The specific gravity of aluminum is about 1/3 of copper, and the conductivity of aluminum is about 2/3 of copper (pure aluminum is about 66% IACS when pure copper is used as the standard for 100% IACS). In order to pass the same current as a pure copper conductor, the cross-sectional area of a pure aluminum conductor needs to be about 1.5 times that of a pure copper conductor, but the weight is still about half that of copper. is there.
The above% IACS represents the electrical conductivity when the resistivity 1.7241 × 10 −8 Ωm of universal standard annealed copper (International Annealed Copper Standard) is 100% IACS.
　そのアルミニウムを移動体の電気配線体の導体として用いるためには幾つかの課題があり、ひとつに耐屈曲疲労特性の向上がある。移動体の電気配線体に使用されるアルミニウム導体に耐屈曲疲労特性が要求されるのは、ドアなどに取り付けられたワイヤーハーネスではドアの開閉により繰り返し曲げ応力を受けるためである。アルミニウムなどの金属材料は、一回の負荷では破断しないような低い荷重でもドアの開閉のように荷重を加えたり除いたりを繰り返し行なうと、ある繰り返し回数で破断する疲労破壊が生じる。前記アルミニウム導体が開閉部に用いられたとき、耐屈曲疲労特性が悪いとその使用中に導体が破断することが懸念され、耐久性、信頼性に欠けるという問題を生ずる。
　一般に強度の高い材料ほど疲労特性は良好と言われている。そこで、強度の高いアルミニウム導体を適用すればよいが、ワイヤーハーネスはその設置時の取り回し（車体への取り付け作業）がしやすいことが要求されているために、一般的には柔軟性が確保できる鈍し材（焼鈍材）が使われていることが多い。 There are several problems in using aluminum as a conductor of an electric wiring body of a moving body, and one is improvement of bending fatigue resistance. The reason why the aluminum conductor used for the electric wiring body of the moving body is required to have bending fatigue resistance is that the wire harness attached to the door or the like is repeatedly subjected to bending stress by opening and closing the door. When a metal material such as aluminum is repeatedly applied and removed such as opening and closing of a door even at a low load that does not break at a single load, fatigue failure that breaks at a certain number of repetitions occurs. When the aluminum conductor is used for an opening / closing portion, if the bending fatigue resistance is poor, there is a concern that the conductor may break during use, resulting in a problem of lack of durability and reliability.
Generally, it is said that a material having higher strength has better fatigue characteristics. Therefore, a high-strength aluminum conductor may be applied. However, since the wire harness is required to be easily handled (installation work on the vehicle body) at the time of installation, in general, flexibility can be secured. Dull material (annealed material) is often used.
　よって、移動体の電気配線体に使用されるアルミニウム導体には、取扱い及び取り付け時に必要となる強度及び柔軟性、電気を多く流すために必要となる導電率に加えて、耐屈曲疲労特性の優れた材料が求められている。 Therefore, the aluminum conductor used for the electric wiring body of the moving body has excellent bending fatigue resistance in addition to the strength and flexibility required for handling and mounting, and the conductivity required to flow a lot of electricity. Materials are needed.
　このような要求のある用途に対して、送電線用アルミニウム合金線材（ＪＩＳ　Ａ１０６０やＪＩＳ　Ａ１０７０）を代表とする純アルミニウム系では、ドアなどの開閉で生じる繰り返し曲げ応力に十分耐えることはできない。また、種々の添加元素を加えた合金化は強度には優れるものの、アルミニウム中への添加元素の固溶現象により導電率の低下を招くこと、柔軟性が低下すること、アルミニウム中に過剰な金属間化合物を形成することで伸線加工中に金属間化合物起因の断線が生じることが問題であった。そのため、添加元素を限定、選択して断線しないことを必須とし、導電率低下、柔軟性低下を防ぎ、強度及び耐屈曲疲労特性を向上する必要があった。 For such demanding applications, pure aluminum systems such as aluminum alloy wire rods for power transmission lines (JIS A1060 and JIS A1070) cannot sufficiently withstand repeated bending stresses that occur when doors are opened and closed. Although alloying with various additive elements is excellent in strength, it causes a decrease in electrical conductivity due to the solid solution phenomenon of the additive elements in aluminum, decreases flexibility, and excessive metals in aluminum. It was a problem that a wire breakage caused by an intermetallic compound occurred during wire drawing by forming an intermetallic compound. Therefore, it is essential to limit and select the additive element and not to disconnect, to prevent a decrease in conductivity and a decrease in flexibility, and to improve strength and bending fatigue resistance.
　移動体の電気配線体に用いられるアルミニウム導体として代表的なものに特許文献１～４に記載のものがある。しかし下記のように、いずれの特許文献記載の発明も、さらに解決すべき課題を有する。
　特許文献１の発明は、仕上げ焼鈍を行っていないため、車体での取り付け作業時に必要な柔軟性が確保できない。
　特許文献２の発明は、仕上げ焼鈍の開示があるが、その条件は、優れた柔軟性を保持したまま、耐屈曲疲労特性や導電率等を向上させるように金属間化合物を制御可能な条件とは異なる。
　特許文献３の発明は、Ｍｇ及びＳｉの量が多いため、金属間化合物を適切に制御することができず、伸線加工などの際に断線の原因となる。
　特許文献４の発明は、添加元素にアンチモン（Ｓｂ）を含んでいるため、環境負荷の観点から、代替製品に置き換えられつつある技術である。 Representative examples of aluminum conductors used for electric wiring bodies of moving bodies include those described in Patent Documents 1 to 4. However, as described below, the inventions described in any of the patent documents have further problems to be solved.
Since the invention of Patent Document 1 does not perform finish annealing, it cannot secure the flexibility required for the mounting work on the vehicle body.
The invention of Patent Document 2 discloses finish annealing, and the conditions are such that the intermetallic compound can be controlled so as to improve the bending fatigue resistance and conductivity while maintaining excellent flexibility. Is different.
In the invention of Patent Document 3, since the amounts of Mg and Si are large, the intermetallic compound cannot be appropriately controlled, which causes disconnection during wire drawing.
The invention of Patent Document 4 is a technique that is being replaced with an alternative product from the viewpoint of environmental load because it contains antimony (Sb) as an additive element.
特開２００６－１９１６３号公報JP 2006-19163 A 特開２００６－２５３１０９号公報JP 2006-253109 A 特開２００８－１１２６２０号公報JP 2008-112620 A 特公昭５５－４５６２６号公報Japanese Patent Publication No. 55-45626
　本発明は、十分な導電率と引張強度を有し、耐屈曲疲労特性、柔軟性などに優れたアルミニウム合金導体の提供を課題とする。 An object of the present invention is to provide an aluminum alloy conductor having sufficient electrical conductivity and tensile strength, and excellent in bending fatigue resistance, flexibility and the like.
　本発明者らは種々検討を重ね、特定の添加元素を添加したアルミニウム合金について、鋳造冷却速度、中間焼鈍、仕上げ焼鈍などの製造条件を制御することにより２種類の金属間化合物の粒子径及び面積率を制御して、優れた耐屈曲疲労特性、強度、柔軟性及び導電率を具備するアルミニウム合金導体を製造しうることを見い出し、この知見に基づき本発明を完成するに至った。 The inventors of the present invention have made various studies, and by controlling the production conditions such as casting cooling rate, intermediate annealing, and finish annealing for the aluminum alloy to which a specific additive element is added, the particle size and area of two kinds of intermetallic compounds. It has been found that an aluminum alloy conductor having excellent bending fatigue resistance, strength, flexibility and electrical conductivity can be produced by controlling the rate, and the present invention has been completed based on this finding.
　すなわち、本発明は、以下の解決手段を提供するものである。
（１）Ｆｅを０．４～０．９ｍａｓｓ％を含有し、残部Ａｌと不可避不純物からなるアルミニウム合金導体であって、
前記導体中に２種類の金属間化合物Ａ、Ｂが存在し、
前記金属間化合物Ａの粒子径は０．１μｍ以上２μｍ以下の範囲であり、
前記金属間化合物Ｂの粒子径は０．０３μｍ以上０．１μｍ未満の範囲であり、
前記導体中の任意の範囲における、前記金属間化合物Ａの面積率ａ、前記金属間化合物Ｂの面積率ｂが、それぞれ１％　≦　ａ　≦　６％、１％　≦　ｂ　≦　５％を満足することを特徴とするアルミニウム合金導体。
（２）Ｆｅを０．４～０．９ｍａｓｓ％と、Ｚｒを０．０１～０．４ｍａｓｓ％とを含有し、残部Ａｌと不可避不純物からなるアルミニウム合金導体であって、
前記導体中に２種類の金属間化合物Ａ、Ｂが存在し、
前記金属間化合物Ａの粒子径は０．１μｍ以上２μｍ以下の範囲であり、
前記金属間化合物Ｂの粒子径は０．０３μｍ以上０．１μｍ未満の範囲であり、
前記導体中の任意の範囲における、前記金属間化合物Ａの面積率ａ、前記金属間化合物Ｂの面積率ｂが、それぞれ１％　≦　ａ　≦　６％、１％　≦　ｂ　≦　７．５％を満足することを特徴とするアルミニウム合金導体。
（３）前記導体の製造工程の最後に急熱、急冷の工程を含む連続通電熱処理が施されることにより、伸線方向の垂直断面における結晶粒径が１～１５μｍとなされる（１）または（２）に記載のアルミニウム合金導体。
（４）引張強度が８０ＭＰａ以上、及び導電率が６０％ＩＡＣＳ以上である（１）～（３）のいずれか１項に記載のアルミニウム合金導体。
（５）引張破断伸びが１０％以上である（１）～（４）のいずれか１項に記載のアルミニウム合金導体。
（６）再結晶組織を有する（１）～（５）のいずれか１項に記載のアルミニウム合金導体。
（７）前記導体が移動体内で、バッテリーケーブル、ハーネス、またはモータ用線材として用いられることを特徴とする（１）～（６）のいずれか１項に記載のアルミニウム合金導体。
（８）前記導体が車両、電車、または航空機に用いられることを特徴とする（１）～（７）のいずれか１項に記載のアルミニウム合金導体。 That is, the present invention provides the following solutions.
(1) An aluminum alloy conductor containing Fe in an amount of 0.4 to 0.9 mass% and comprising the balance Al and inevitable impurities,
Two types of intermetallic compounds A and B exist in the conductor,
The particle size of the intermetallic compound A is in the range of 0.1 μm to 2 μm,
The particle size of the intermetallic compound B is in the range of 0.03 μm or more and less than 0.1 μm,
The area ratio a of the intermetallic compound A and the area ratio b of the intermetallic compound B in an arbitrary range in the conductor satisfy 1% ≦ a ≦ 6% and 1% ≦ b ≦ 5%, respectively. Aluminum alloy conductor characterized by
(2) An aluminum alloy conductor containing 0.4 to 0.9 mass% of Fe and 0.01 to 0.4 mass% of Zr, the balance being Al and inevitable impurities,
Two types of intermetallic compounds A and B exist in the conductor,
The particle size of the intermetallic compound A is in the range of 0.1 μm to 2 μm,
The particle size of the intermetallic compound B is in the range of 0.03 μm or more and less than 0.1 μm,
The area ratio a of the intermetallic compound A and the area ratio b of the intermetallic compound B in an arbitrary range in the conductor satisfy 1% ≦ a ≦ 6% and 1% ≦ b ≦ 7.5%, respectively. An aluminum alloy conductor characterized by:
(3) A continuous energization heat treatment including a rapid heating and rapid cooling process is performed at the end of the manufacturing process of the conductor, so that the crystal grain size in the vertical cross section in the wire drawing direction is 1 to 15 μm (1) or The aluminum alloy conductor according to (2).
(4) The aluminum alloy conductor according to any one of (1) to (3), wherein the tensile strength is 80 MPa or more and the electrical conductivity is 60% IACS or more.
(5) The aluminum alloy conductor according to any one of (1) to (4), which has a tensile elongation at break of 10% or more.
(6) The aluminum alloy conductor according to any one of (1) to (5), which has a recrystallized structure.
(7) The aluminum alloy conductor according to any one of (1) to (6), wherein the conductor is used as a battery cable, a harness, or a motor wire in the moving body.
(8) The aluminum alloy conductor according to any one of (1) to (7), wherein the conductor is used in a vehicle, a train, or an aircraft.
　本発明のアルミニウム合金導体は強度、柔軟性及び導電率に優れ、移動体に搭載されるバッテリーケーブル、ハーネスあるいはモータ用導体として有用なもので、優れた耐屈曲疲労特性が求められるドアやトランク、ボンネットなどにも好適に用いることができる。 The aluminum alloy conductor of the present invention is excellent in strength, flexibility and electrical conductivity, and is useful as a battery cable, harness or motor conductor mounted on a moving body, doors and trunks that require excellent bending fatigue resistance, It can be suitably used for a bonnet or the like.
　本発明の上記及び他の特徴及び利点は、適宜添付の図面を参照して、下記の記載からより明らかになるであろう。 The above and other features and advantages of the present invention will become more apparent from the following description with reference to the accompanying drawings as appropriate.
実施例で行なった繰返破断回数を測定する試験の説明図である。It is explanatory drawing of the test which measures the frequency | count of repeated fracture performed in the Example.
　本発明の好ましい第１の実施態様は、Ｆｅを０．４～０．９ｍａｓｓ％を含有し、残部Ａｌと不可避不純物からなるアルミニウム合金導体であって、
前記導体中に２種類の金属間化合物Ａ、Ｂが存在し、
前記金属間化合物Ａの粒子径は０．１μｍ以上２μｍ以下の範囲であり、
前記金属間化合物Ｂの粒子径は０．０３μｍ以上０．１μｍ未満の範囲であり、
前記導体中の任意の範囲における、前記金属間化合物Ａの面積率ａ、前記金属間化合物Ｂの面積率ｂが、それぞれ１％　≦　ａ　≦　６％、１％　≦　ｂ　≦　５％を満足する。 A preferred first embodiment of the present invention is an aluminum alloy conductor containing 0.4 to 0.9 mass% of Fe and comprising the balance Al and inevitable impurities,
Two types of intermetallic compounds A and B exist in the conductor,
The particle size of the intermetallic compound A is in the range of 0.1 μm to 2 μm,
The particle size of the intermetallic compound B is in the range of 0.03 μm or more and less than 0.1 μm,
The area ratio a of the intermetallic compound A and the area ratio b of the intermetallic compound B in an arbitrary range in the conductor satisfy 1% ≦ a ≦ 6% and 1% ≦ b ≦ 5%, respectively.
　本実施態様において、Ｆｅの含有量を０．４～０．９ｍａｓｓ％とするのは、主にＡｌ－Ｆｅ系の金属間化合物による様々な効果を利用するためである。Ｆｅはアルミニウム中には６５５℃において０．０５ｍａｓｓ％しか固溶せず、室温では更に少ない。残りはＡｌ－Ｆｅ、Ａｌ－Ｆｅ－Ｓｉなどの金属間化合物として晶出または析出する。この晶出物または析出物は結晶粒の微細化材として働くと共に、強度、及び耐屈曲疲労特性を向上させる。Ｆｅの含有量が少なすぎるとこれらの効果が不十分であり、多すぎると晶出物の粗大化により伸線加工性が悪く、目的の耐屈曲疲労特性が得られず、柔軟性も低下する。また過飽和固溶状態となり導電率も低下する。Ｆｅの含有量は好ましくは０．４～０．８ｍａｓｓ％、さらに好ましくは０．５～０．７ｍａｓｓ％である。 In the present embodiment, the reason why the Fe content is set to 0.4 to 0.9 mass% is mainly to use various effects of the Al—Fe-based intermetallic compound. Fe dissolves only 0.05 mass% in aluminum at 655 ° C., and is even less at room temperature. The remainder crystallizes or precipitates as an intermetallic compound such as Al—Fe or Al—Fe—Si. This crystallized product or precipitate acts as a crystal grain refining material, and improves strength and bending fatigue resistance. If the Fe content is too small, these effects are insufficient, and if it is too much, the crystallized material becomes coarse and the wire drawing workability is poor, the desired bending fatigue resistance cannot be obtained, and the flexibility also decreases. . Moreover, it will be in a supersaturated solid solution state and electrical conductivity will also fall. The Fe content is preferably 0.4 to 0.8 mass%, more preferably 0.5 to 0.7 mass%.
　本発明の好ましい第２の実施態様は、Ｆｅを０．４～０．９ｍａｓｓ％と、Ｚｒを０．０１～０．４ｍａｓｓ％とを含有し、残部Ａｌと不可避不純物からなるアルミニウム合金導体であって、
前記導体中に２種類の金属間化合物Ａ、Ｂが存在し、
前記金属間化合物Ａの粒子径は０．１μｍ以上２μｍ以下であり、
前記金属間化合物Ｂの粒子径は０．０３μｍ以上０．１μｍ未満であり、
前記金属間化合物Ａの面積率ａ、前記金属間化合物Ｂの面積率ｂが、１％　≦　ａ　≦　６％、１％　≦　ｂ　≦　７．５％を満足する。 A preferred second embodiment of the present invention is an aluminum alloy conductor containing 0.4 to 0.9 mass% Fe and 0.01 to 0.4 mass% Zr, and the balance being Al and inevitable impurities. And
Two types of intermetallic compounds A and B exist in the conductor,
The particle size of the intermetallic compound A is 0.1 μm or more and 2 μm or less,
The particle size of the intermetallic compound B is 0.03 μm or more and less than 0.1 μm,
The area ratio a of the intermetallic compound A and the area ratio b of the intermetallic compound B satisfy 1% ≦ a ≦ 6% and 1% ≦ b ≦ 7.5%.
　第２の実施態様では、合金組成については上述の第１の実施態様の合金組成に加えて、さらにＺｒを０．０１～０．４ｍａｓｓ％含有させたものである。ＺｒはＡｌと金属間化合物を形成し、また、Ａｌ中に固溶して、アルミニウム合金導体の強度と耐熱性の向上に寄与する。Ｚｒの含有量が少なすぎるとその効果が期待できず、多すぎると溶解温度が高くなり伸線形成が困難になる。また、導電率、柔軟性の低下を招き、耐屈曲疲労特性も悪くなる。Ｚｒの含有量は、好ましくは０．１～０．３５ｍａｓｓ％、より好ましくは０．１５～０．３ｍａｓｓ％である。
　その他の合金組成とその作用については上述の第１の実施態様と同様である。 In the second embodiment, the alloy composition includes 0.01 to 0.4 mass% of Zr in addition to the alloy composition of the first embodiment described above. Zr forms an intermetallic compound with Al, and forms a solid solution in Al, thereby contributing to the improvement of the strength and heat resistance of the aluminum alloy conductor. If the Zr content is too small, the effect cannot be expected. If the Zr content is too large, the melting temperature becomes high and it becomes difficult to form a drawn wire. In addition, the conductivity and flexibility are lowered, and the bending fatigue resistance is also deteriorated. The Zr content is preferably 0.1 to 0.35 mass%, more preferably 0.15 to 0.3 mass%.
Other alloy compositions and their actions are the same as in the first embodiment described above.
　本発明のアルミニウム合金導体には、上記の成分以外に金属間化合物の寸法（粒子径）と面積率を規定することにより、所望の優れた耐屈曲疲労特性、強度、柔軟性及び導電率を具備したアルミニウム合金導体を得ることができる。 In addition to the above components, the aluminum alloy conductor of the present invention has desired excellent bending fatigue resistance, strength, flexibility and electrical conductivity by defining the size (particle diameter) and area ratio of the intermetallic compound. An aluminum alloy conductor can be obtained.
（金属間化合物の寸法（粒子径）と面積率）
　本発明は前記第１及び第２の実施態様に示すように粒子径の異なる２種類の金属間化合物をそれぞれ所定の面積率で含有する。ここで、金属間化合物とは、結晶粒内に存在する、晶出物、析出物などの粒子である。主として、晶出物は溶解鋳造時に形成され、析出物は中間焼鈍及び仕上げ焼鈍で形成される、例えば、Ａｌ－Ｆｅ、Ａｌ－Ｆｅ－Ｓｉ、Ａｌ－Ｚｒ等の粒子である。なお、面積率は本合金に含まれる金属間化合物の割合を面積で表したものであり、ＴＥＭにより観察した写真を基に、以下に詳述するようにして算出できる。
　金属間化合物Ａは主にＡｌ－Ｆｅにより構成され、一部にＡｌ－Ｆｅ－Ｓｉ、Ａｌ－Ｚｒ等が含まれる。これらの金属間化合物は結晶粒の微細化材として働くと共に、強度、及び耐屈曲疲労特性を向上させる。金属間化合物Ａの面積率ａを１％　≦　ａ　≦　６％としたのは、少なすぎるとこれらの効果が不十分であり、多すぎると金属間化合物を起因として断線が起こりやすく、目的の耐屈曲疲労特性が得られず、柔軟性も低下する。
　金属間化合物Ｂは主にＡｌ－Ｆｅ－Ｓｉ、Ａｌ－Ｚｒにより構成される。これらの金属間化合物は析出により強度、及び耐屈曲疲労特性を向上させる。金属間化合物Ｂの面積率ｂを第１の実施態様では１％　≦　ｂ　≦　５％、第２の実施態様では１％　≦　ｂ　≦　７．５％としたのは、少なすぎるとこれらの効果が不十分であり、多すぎると析出過剰により断線の原因となるためである。また柔軟性も低下する。 (Dimensions (particle diameter) and area ratio of intermetallic compounds)
As shown in the first and second embodiments, the present invention contains two kinds of intermetallic compounds having different particle diameters at a predetermined area ratio. Here, an intermetallic compound is particles, such as a crystallized substance and a precipitate, which exist in crystal grains. The crystallized material is mainly formed during melt casting, and the precipitate is formed by intermediate annealing and finish annealing, for example, particles such as Al—Fe, Al—Fe—Si, and Al—Zr. The area ratio represents the ratio of intermetallic compounds contained in the present alloy in terms of area, and can be calculated as described in detail below based on a photograph observed by TEM.
The intermetallic compound A is mainly composed of Al—Fe, and a part thereof includes Al—Fe—Si, Al—Zr and the like. These intermetallic compounds work as crystal grain refiners and improve strength and bending fatigue resistance. The reason why the area ratio a of the intermetallic compound A is 1% ≦ a ≦ 6% is that these effects are insufficient if the amount is too small, and if the amount is too large, disconnection is likely to occur due to the intermetallic compound. Flexural fatigue characteristics cannot be obtained and flexibility is also reduced.
The intermetallic compound B is mainly composed of Al—Fe—Si and Al—Zr. These intermetallic compounds improve strength and bending fatigue resistance by precipitation. 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. This is because it is insufficient, and if it is too much, it causes disconnection due to excessive precipitation. Also, flexibility is reduced.
　本発明の第１及び第２の実施態様において、２種類の寸法の金属間化合物Ａ、Ｂにおいて、面積率を上記の値とするには、それぞれの合金組成を前述の範囲に設定する必要がある。そして、鋳造冷却速度、中間焼鈍温度、仕上げ焼鈍条件などを適切に制御することにより実現できる。 In the first and second embodiments of the present invention, in the intermetallic compounds A and B having two types of dimensions, in order to set the area ratio to the above value, it is necessary to set each alloy composition within the above-described range. is there. And it is realizable by controlling appropriately a casting cooling rate, intermediate annealing temperature, finish annealing conditions, etc.
　鋳造冷却速度とは、アルミニウム合金鋳塊の凝固開始から２００℃までの平均の冷却速度のことである。この冷却速度を変える方法として、例えば、以下の３つの方法が挙げられる。すなわち、（１）鉄製鋳型のサイズ（肉厚）を変える、（２）鋳型下面に水冷モールドを設けて強制冷却する（水量を変えることでも冷却速度が変わる）、（３）溶湯の鋳込み量を変えるといったものである。鋳造冷却速度が遅すぎると、Ａｌ－Ｆｅ系の晶出物が粗大化することにより目的の組織が得られず、割れが生じやすくなる。速すぎると、Ｆｅの過剰固溶が起き、目的の組織が得られず、導電率の低下を招く。場合によっては鋳造割れも起こりうる。鋳造冷却速度は通常１～２０℃／秒とし、好ましくは５～１５℃／秒である。 The casting cooling rate is an average cooling rate from the start of solidification of the aluminum alloy ingot to 200 ° C. As a method for changing the cooling rate, for example, the following three methods can be cited. That is, (1) change the size (thickness) of the iron mold, (2) provide a water cooling mold on the lower surface of the mold and forcibly cool (the cooling speed also changes by changing the amount of water), (3) the amount of molten metal cast Change. If the casting cooling rate is too slow, the Al—Fe-based crystallized product becomes coarse, and the desired structure cannot be obtained, and cracking tends to occur. If it is too fast, an excessive solid solution of Fe occurs, the target structure cannot be obtained, and the electrical conductivity is lowered. In some cases, casting cracks can also occur. The casting cooling rate is usually 1 to 20 ° C./second, preferably 5 to 15 ° C./second.
　中間焼鈍温度とは、伸線途中に熱処理を施す際の温度のことである。中間焼鈍は主に伸線加工で硬くなった線材の柔軟性を取り戻すために行なう。中間焼鈍温度が低すぎる場合、再結晶が不十分なため耐力が過剰となり柔軟性が確保できず、後の伸線加工で断線を起し線材が得られなくなる恐れが高まる。高すぎる場合、過焼鈍状態となり再結晶粒粗大化が起き柔軟性が著しく低下し、後の伸線加工で断線を起し線材が得られなくなる恐れが高まる。中間焼鈍温度は通常３００～４５０℃とし、好ましくは３５０～４５０℃である。中間焼鈍の時間は、通常３０分以上とする。３０分未満であると、再結晶粒形成及び成長に必要な時間が足りず、線材の柔軟性を取り戻すことができないためである。好ましくは１～６時間である。また、中間焼鈍時の熱処理温度から１００℃までの平均冷却速度は特に規定しないが、０．１～１０℃／分が望ましい。 The intermediate annealing temperature is the temperature at which heat treatment is performed during wire drawing. The intermediate annealing is performed mainly to regain the flexibility of the wire that has been hardened by wire drawing. If the intermediate annealing temperature is too low, the recrystallization is insufficient and the yield strength becomes excessive, so that flexibility cannot be secured, and there is a high possibility that the wire will not be obtained due to the subsequent wire drawing. When too high, it will be in an over-annealed state, recrystallization grain coarsening will occur and flexibility will fall remarkably, and the possibility that a wire will not be obtained due to breakage in the subsequent wire drawing will increase. The intermediate annealing temperature is usually 300 to 450 ° C, preferably 350 to 450 ° C. The time for the intermediate annealing is usually 30 minutes or more. This is because if it is less than 30 minutes, the time required for the formation and growth of recrystallized grains is insufficient, and the flexibility of the wire cannot be recovered. Preferably it is 1 to 6 hours. The average cooling rate from the heat treatment temperature during intermediate annealing to 100 ° C. is not particularly specified, but is preferably 0.1 to 10 ° C./min.
　仕上げ焼鈍は、例えば、２つの電極輪を連続的に通過する線材に電流を流すことによって自身から発生するジュール熱により焼鈍する連続通電熱処理によって行なう。連続通電熱処理は、急熱、急冷の工程を含み、線材温度と時間で制御し線材を焼鈍することができる。冷却は、急熱後、水中に線材を連続的に通過させることによって行なう。焼鈍時の線材温度が低すぎるもしくは高すぎる場合、焼鈍時間が短すぎるもしくは長すぎる場合の一方または両方の場合には、目的の組織が得られなくなる。さらに、焼鈍時の線材温度が低すぎる場合、焼鈍時間が短すぎる場合の一方または両方の場合には車載取り付けの際に必要な柔軟性が得られず、焼鈍時の線材温度が高すぎる場合、焼鈍時間が長すぎる場合の一方または両方の場合には強度が低下し、耐屈曲疲労特性も悪くなる。すなわち、線材温度ｙ（℃）、焼鈍時間ｘ（秒）で表される数式を用いると、０．０３≦ｘ≦０．５５の範囲で２６ｘ－０．６＋３７７≦ｙ≦１９ｘ－０．６＋４７７を満たす焼鈍条件である必要がある。線材温度は、線材で最も高くなる水中に通過する直前の温度を表す。
　なお、仕上げ焼鈍は連続通電熱処理の他に、急熱、急冷過程を含む、例えば、高温に保持した焼鈍炉中を線材が連続的に通過して焼鈍させる走間焼鈍や、磁場中を線材が連続的に通過して焼鈍させる誘導加熱でもよい。雰囲気や熱伝達率が異なるため焼鈍条件は連続通電熱処理と同一条件ではないが、これらの急熱、急冷過程を含む、走間焼鈍や誘導加熱の場合であっても、所定の金属間化合物の析出状態を有してなる本発明のアルミニウム合金導体が得られるように、代表例としての前記の連続通電熱処理における焼鈍条件を参考に仕上げ焼鈍条件（熱履歴）を適切に制御することで、本発明のアルミニウム合金導体を作製することができる。 The finish annealing is performed, for example, by continuous energization heat treatment in which annealing is performed by Joule heat generated from itself by passing an electric current through a wire that passes through two electrode wheels. The continuous energization heat treatment includes rapid heating and rapid cooling steps, and can be annealed by controlling the wire temperature and time. Cooling is performed by passing the wire continuously through water after rapid heating. If the wire temperature during annealing is too low or too high, or if one or both of the annealing times are too short or too long, the desired structure cannot be obtained. Furthermore, if the wire temperature during annealing is too low, if one or both of the annealing time is too short, the necessary flexibility when mounting on the vehicle is not obtained, if the wire temperature during annealing is too high, In one or both of cases where the annealing time is too long, the strength is lowered and the bending fatigue resistance is also deteriorated. That is, the wire temperature y (° C.), the use of equations represented by annealing time x (seconds), 26x -0.6 + 377 within a range of 0.03 ≦ x ≦ 0.55 ≦ y ≦ 19x -0.6 It is necessary that the annealing conditions satisfy +477. The wire temperature represents the temperature immediately before passing through the water, which is the highest in the wire.
Note that finish annealing includes rapid heating and quenching processes in addition to continuous energization heat treatment, for example, running annealing in which the wire continuously anneals through an annealing furnace maintained at a high temperature, and the wire in the magnetic field. It may be induction heating that passes and anneals continuously. The annealing conditions are not the same as those for continuous energization heat treatment because the atmosphere and heat transfer coefficient are different, but even in the case of running annealing and induction heating, including these rapid heating and quenching processes, the prescribed intermetallic compound By appropriately controlling the finish annealing conditions (thermal history) with reference to the annealing conditions in the continuous energization heat treatment as a representative example so that the aluminum alloy conductor of the present invention having a precipitation state can be obtained, The aluminum alloy conductor of the invention can be produced.
（結晶粒径）
　本発明ではアルミニウム合金導体の伸線方向の垂直断面における結晶粒径を１～１５μｍとする。この理由は、粒径が小さすぎると部分再結晶組織が残存して引張破断伸びが著しく低下するためであり、大きすぎると粗大な組織を形成して変形挙動が不均一となり、同様に引張破断伸びが低下、さらに強度が著しく低下するためである。結晶粒径は、好ましくは１～１０μｍである。 (Crystal grain size)
In the present invention, the crystal grain size in the vertical cross section of the aluminum alloy conductor in the wire drawing direction is 1 to 15 μm. The reason for this is that if the particle size is too small, the partially recrystallized structure remains and the tensile elongation at break is remarkably reduced, and if it is too large, a coarse structure is formed and the deformation behavior becomes non-uniform, and similarly the tensile break This is because the elongation is lowered and the strength is significantly lowered. The crystal grain size is preferably 1 to 10 μm.
（引張強度と導電率）
　本発明のアルミニウム合金導体は、引張強度（ＴＳ）が８０ＭＰａ以上、及び導電率が６０％ＩＡＣＳ以上であり、好ましくは引張強度が８０～１５０ＭＰａ及び導電率が６０～６５％ＩＡＣＳ、より好ましくは引張強度が１００～１４０ＭＰａ及び導電率が６１～６４％ＩＡＣＳである。
　引張強度と導電率は相反する性質のものであり、引張強度が高いほど導電率が低く、逆に引張強度が低い純アルミニウムは導電率が高い。アルミニウム合金導体を考えた場合、引張強度が８０ＭＰａ未満では取り扱いを含めて弱々しく、工業用導体として使用することが難しい。動力線に用いる場合には数十Ａ（アンペア）の高電流が流れるため、導電率は６０％ＩＡＣＳ以上であることが望まれる。 (Tensile strength and conductivity)
The aluminum alloy conductor of the present invention has a tensile strength (TS) of 80 MPa or more and a conductivity of 60% IACS or more, preferably a tensile strength of 80 to 150 MPa and a conductivity of 60 to 65% IACS, more preferably tensile. The strength is 100 to 140 MPa and the conductivity is 61 to 64% IACS.
Tensile strength and electrical conductivity have contradictory properties. The higher the tensile strength, the lower the electrical conductivity, and conversely, pure aluminum with a low tensile strength has a higher electrical conductivity. When an aluminum alloy conductor is considered, if the tensile strength is less than 80 MPa, it is weak including handling, and it is difficult to use it as an industrial conductor. When used for a power line, a high current of several tens of A (amperes) flows, so that the conductivity is desirably 60% IACS or more.
（柔軟性）
　本発明のアルミニウム合金導体は、十分な柔軟性を有する。これは前述の仕上げ焼鈍を行なうことにより得ることができる。本発明ではアルミニウム合金導体の柔軟性の指標として引張破断伸びを用い、好ましくは１０％以上とする。この理由は、引張破断伸びが小さすぎると前述の通り電気配線体設置時の取り回し（例えば車体への取り付け作業）がしにくくなるためであり、大きすぎると強度不足となり取り回し時に弱々しく、断線の原因になりうるためである。引張破断伸びは、より好ましくは２０～５０％、さらに好ましくは２５～４５％である。 (Flexibility)
The aluminum alloy conductor of the present invention has sufficient flexibility. This can be obtained by performing the above-described finish annealing. In the present invention, the tensile elongation at break is used as an index of the flexibility of the aluminum alloy conductor, preferably 10% or more. The reason for this is that if the tensile elongation at break is too small, it becomes difficult to handle the wiring (for example, mounting work on the vehicle body) as described above. This is because it may cause The tensile elongation at break is more preferably 20 to 50%, still more preferably 25 to 45%.
　本発明のアルミニウム合金導体は、[１]溶解、[２]鋳造、[３]熱間または冷間加工（溝ロール加工など）、[４]伸線加工、[５]熱処理（中間焼鈍）、[６]伸線加工、[７]熱処理（仕上げ焼鈍）の各工程を経て製造することができる。 The aluminum alloy conductor of the present invention includes [1] melting, [2] casting, [3] hot or cold processing (groove roll processing, etc.), [4] wire drawing, [5] heat treatment (intermediate annealing), It can be manufactured through steps of [6] wire drawing and [7] heat treatment (finish annealing).
［１］溶解
　本発明のアルミニウム合金組成を得るには、Ｆｅ及びＡｌ、またはＦｅ、Ｚｒ及びＡｌを所望の濃度となるような分量で溶製する。 [1] Melting In order to obtain the aluminum alloy composition of the present invention, Fe and Al, or Fe, Zr and Al are melted in such amounts that a desired concentration is obtained.
［２］鋳造及び［３］熱間または冷間加工（溝ロール加工など）
　次いで、例えば、鋳造輪とベルトを組み合わせたプロペルチ式の連続鋳造圧延機を用いて、溶湯を水冷した鋳型で連続的に鋳造しながら圧延を行ない、約１０ｍｍφの棒材とする。このときの鋳造冷却速度は上述の通り通常１～２０℃／秒である。鋳造及び熱間圧延は、鋳造冷却速度を１～２０℃／秒としたビレット鋳造、及び押出法などにより行なってもよい。 [2] Casting and [3] Hot or cold processing (groove roll processing, etc.)
Next, for example, using a Properti type continuous casting and rolling machine in which a casting wheel and a belt are combined, rolling is performed while continuously casting the molten metal in a water-cooled mold to obtain a rod of about 10 mmφ. The casting cooling rate at this time is usually 1 to 20 ° C./second as described above. Casting and hot rolling may be performed by billet casting at a casting cooling rate of 1 to 20 ° C./second, an extrusion method, or the like.
［４］伸線加工
　次いで、表面の皮むきを実施して、９～９．５ｍｍφとし、これを伸線加工する。ここで、伸線加工前の線材断面積をＡ０、伸線加工後の線材断面積をＡ１とすると、η＝ｌｎ（Ａ０／Ａ１）で表される加工度は、１以上６以下が望ましい。１未満であると、次工程の熱処理時、再結晶粒が粗大化し強度及び引張破断伸びが著しく低下し、断線の原因にもなる。６を越えると、加工硬化しすぎて伸線加工が困難となり、伸線加工中に断線するなど品質の面で問題がある。線材表面の皮むきは、行なうことによって表面の清浄化がなされるが、行なわなくてもよい。 [4] Wire drawing Next, the surface is peeled to 9 to 9.5 mmφ, and this is drawn. Here, when the wire cross-sectional area before wire drawing is A 0 , and the wire cross-sectional area after wire drawing is A 1 , the degree of work represented by η = ln (A 0 / A 1 ) is 1 or more and 6 The following is desirable. If it is less than 1, the recrystallized grains become coarse during the heat treatment in the next step, and the strength and tensile elongation at break are remarkably reduced, which may cause disconnection. If it exceeds 6, work hardening becomes too difficult to draw, and there is a problem in terms of quality, such as disconnection during drawing. Although the surface of the wire is peeled to clean the surface, it need not be performed.
［５］熱処理（中間焼鈍）
　冷間伸線した加工材に中間焼鈍を施す。中間焼鈍の条件は上述の通り通常３００～４５０℃３０分以上である。 [5] Heat treatment (intermediate annealing)
Intermediate annealing is applied to the cold-drawn workpiece. The conditions for the intermediate annealing are usually 300 to 450 ° C. for 30 minutes or more as described above.
［６］伸線加工
　さらに伸線加工を施す。この際も加工度は前述の理由により１以上６以下が望ましい。 [6] Wire drawing Further wire drawing is performed. Also in this case, the degree of processing is preferably 1 or more and 6 or less for the reason described above.
［７］熱処理（仕上げ焼鈍）
　冷間伸線した加工材に連続通電熱処理により仕上げ焼鈍を行なう。焼鈍条件は上述の通り線材温度ｙ（℃）、焼鈍時間ｘ（秒）で表される数式を用いると、０．０３≦ｘ≦０．５５の範囲で２６ｘ－０．６＋３７７≦ｙ≦１９ｘ－０．６＋４７７を満たす。 [7] Heat treatment (finish annealing)
Finish annealing is performed on the cold-drawn workpiece by continuous energization heat treatment. As described above, the annealing condition is expressed by the wire temperature y (° C.) and the annealing time x (seconds). In the range of 0.03 ≦ x ≦ 0.55, 26x− 0.6 + 377 ≦ y ≦ 19x -0.6 +477 is satisfied.
　以上のように熱処理を施して作製した本発明のアルミニウム合金導体は再結晶組織を有する。再結晶組織とは、塑性加工により導入される転位などの格子欠陥が少ない結晶粒で構成された組織状態のことである。再結晶組織を有することにより、引張破断伸び、導電率が回復し、十分な柔軟性を得ることが出来る。 The aluminum alloy conductor of the present invention produced by heat treatment as described above has a recrystallized structure. The recrystallized structure is a structure state composed of crystal grains with few lattice defects such as dislocations introduced by plastic working. By having a recrystallized structure, tensile elongation at break and electrical conductivity are recovered, and sufficient flexibility can be obtained.
　本発明を以下の実施例に基づきさらに詳細に説明する。なお本発明は、以下に示す実施例に限定されるものではない。 The present invention will be described in more detail based on the following examples. In addition, this invention is not limited to the Example shown below.
　実施例１～１３、比較例１０１～１１０、２０１
　Ｆｅ及びＡｌ、またはＦｅ、Ｚｒ及びＡｌを表１－１及び表２－１に示す量（質量％）で、プロペルチ式の連続鋳造圧延機を用いて、溶湯を水冷した鋳型で連続的に鋳造しながら圧延を行ない、約１０ｍｍφの棒材とした。このときの鋳造冷却速度は１～２０℃／秒（比較例では０．２℃／秒、５０℃／秒を含む）である。
　次いで、表面の皮むきを実施して、９～９．５ｍｍφとし、これを伸線加工して、２．６ｍｍφとする。次に表１－１及び表２－１に示すように、この冷間伸線した加工材に温度３００～４５０℃（比較例では２００℃、５５０℃を含む）で０．５～４時間（比較例では０．１時間を含む）の中間焼鈍を施し、更に、実施例１～１１、比較例１０１～１１０、２０１では０．３１ｍｍφまで、実施例１２では０．３７ｍｍφまで、実施例１３では０．４３ｍｍφまで伸線加工を行った。
　最後に仕上げ焼鈍として連続通電熱処理を温度４６１～６２１℃（比較例では４３２、４３５、４５０、４６０、６２３℃を含む）、時間０．０３～０．５４秒で行なった。温度はファイバ型放射温度計（ジャパンセンサー株式会社製）で線材の温度が最も高くなる水面直上の温度を測定した。 Examples 1 to 13, Comparative Examples 101 to 110, 201
Continuous casting of Fe and Al, or Fe, Zr and Al in the amounts (mass%) shown in Table 1-1 and Table 2-1, using a Properti-type continuous casting rolling mill with a water-cooled mold. Rolling was performed while making a rod of about 10 mmφ. The casting cooling rate at this time is 1 to 20 ° C./second (including 0.2 ° C./second and 50 ° C./second in the comparative example).
Next, the surface is peeled to 9 to 9.5 mmφ, and this is drawn to 2.6 mmφ. Next, as shown in Table 1-1 and Table 2-1, the cold-drawn processed material was heated to 300 to 450 ° C. (including 200 ° C. and 550 ° C. in the comparative example) for 0.5 to 4 hours ( (Comparative example includes 0.1 hour). Further, in Examples 1 to 11, Comparative Examples 101 to 110 and 201, up to 0.31 mmφ, in Example 12, up to 0.37 mmφ, in Example 13, Drawing was performed to 0.43 mmφ.
Finally, as a final annealing, continuous energization heat treatment was performed at a temperature of 461 to 621 ° C. (including 432, 435, 450, 460, and 623 ° C. in the comparative example) at a time of 0.03 to 0.54 seconds. The temperature was measured with a fiber-type radiation thermometer (manufactured by Japan Sensor Co., Ltd.) immediately above the water surface where the temperature of the wire became highest.
　作製した各々の実施例及び比較例の線材について以下に記す方法により各特性を測定した。その結果を表１－２及び表２－２に示す。 Each characteristic was measured with the method described below about the produced wire of each Example and a comparative example. The results are shown in Table 1-2 and Table 2-2.
（ａ）結晶粒径
　伸線方向に垂直に切り出した供試材の横断面を樹脂で埋め、機械研磨後、電解研磨を行った。電解研磨条件は、研磨液が過塩素酸２０％のエタノール溶液、液温は０～５℃、電圧は１０Ｖ、電流は１０ｍＡ、時間は３０～６０秒である。次いで、結晶粒コントラストを得るため、２％ホウフッ化水素酸を用いて、電圧２０Ｖ、電流２０ｍＡ、時間２～３分の条件でアノーダイジング仕上げを行なった。この組織を２００～４００倍の光学顕微鏡で撮影し、交差法による粒径測定を行った。具体的には、撮影された写真に任意に直線を引いて、その直線の長さと粒界が交わる数を測定して平均粒径を求めた。なお、粒径は５０～１００個が数えられるように直線の長さと本数を変えて評価した。
（ｂ）金属間化合物の同定と、寸法（粒子径）及び面積率
　実施例および比較例の線材を電解研磨薄膜法（ツインジェット研磨法）にて薄膜にして、透過電子顕微鏡（ＴＥＭ）を用い、倍率６０００～３００００倍で任意の範囲を観察した。次いで、エネルギー分散型Ｘ線検出器（ＥＤＸ）を用いて、金属間化合物に電子線を絞り、Ａｌ－Ｆｅ、Ａｌ－Ｆｅ－Ｓｉ、Ａｌ－Ｚｒ系の金属間化合物を検出した。
　金属間化合物の寸法は撮影された写真のスケールから判断し、形状を等体積球相当に換算して算出した。金属間化合物の面積率ａ、ｂは、撮影された写真を基に、金属間化合物Ａについては約５～１０個、金属間化合物Ｂについては２０～５０個をカウントできる範囲を設定して、それぞれの金属間化合物の大きさ及び個数から金属間化合物の面積を算出して、ぞれぞれの金属間化合物の面積をカウント対象とした範囲の面積で割って求めた。
　面積率は上記薄片の試料厚さを０．１５μｍを基準厚さとして算出している。試料厚さが基準厚さと異なる場合、試料厚さを基準厚さに換算して、つまり、（基準厚さ／試料厚さ）を撮影された写真を基に算出した面積率にかけることによって、面積率を算出できる。本実施例および比較例では試料厚さは写真から観察された等厚縞の間隔を観測することにより算出し、すべての試料においてほぼ０．１５μｍであった。
（ｃ）引張強度及び引張破断伸び
　ＪＩＳ　Ｚ　２２４１に準じて各３本ずつ試験し、その平均値を求めた。
（ｄ）導電率
　長さ３００ｍｍの試験片を２０℃（±０．５℃）に保持した恒温漕中で、四端子法を用いて比抵抗を各３本ずつ測定し、その平均導電率を算出した。端子間距離は２００ｍｍとした。
（ｅ）繰返破断回数
　耐屈曲疲労特性の基準として、常温におけるひずみ振幅は±０．１７％とした。耐屈曲疲労特性はひずみ振幅によって変化する。ひずみ振幅が大きい場合疲労寿命は短くなり、ひずみ振幅が小さい場合疲労寿命は長くなる。ひずみ振幅は図１記載の線材１の線径と曲げ冶具２、３の曲率半径により決定することができるため、線材１の線径と曲げ冶具２、３の曲率半径は任意に設定して屈曲疲労試験を実施することが可能である。
　藤井精機株式会社（現　株式会社フジイ）製の両振屈曲疲労試験機を用い、線材に±０．１７％の曲げ歪みが与えられる治具を使用して、繰り返し曲げを実施することにより、繰返破断回数を測定した。繰返破断回数は各４本ずつ測定し、その平均値を求めた。図１の説明図に示すように、線材１を、曲げ治具２及び３の間を１ｍｍ空けて挿入し、冶具２及び３に沿わせるような形で繰り返し運動をさせた。線材の一端は繰り返し曲げが実施できるよう押さえ冶具５に固定し、もう一端には約１０ｇの重り４をぶら下げた。試験中は押さえ冶具５が動くため、それに固定されている線材１も動き、繰り返し曲げが実施できる。繰り返しは１．５Ｈｚ（１秒間に往復１．５回）の条件で行い、線材の試験片１が破断すると、重り４が落下し、カウントを停止する仕組みになっている。
　１日あたりの開閉回数を１０回とし１０年間の使用を想定した場合、開閉回数は３６５００回となる（１年３６５日として計算）。実際に使用される電線は単線ではなく、撚り線構造となり、さらに被覆処理がされているために電線導体への負担は数分の一となる。単線での評価値として十分な耐屈曲疲労特性が確保できる５００００回以上の繰返破断回数が好ましく、より好ましくは７００００回以上である。 (A) Crystal grain size The cross section of the specimen cut out perpendicular to the wire drawing direction was filled with resin, and after mechanical polishing, electrolytic polishing was performed. The electrolytic polishing conditions are: an ethanol solution containing 20% perchloric acid, a liquid temperature of 0 to 5 ° C., a voltage of 10 V, a current of 10 mA, and a time of 30 to 60 seconds. Next, in order to obtain crystal grain contrast, anodic finishing was performed using 2% borohydrofluoric acid under the conditions of a voltage of 20 V, a current of 20 mA, and a time of 2 to 3 minutes. This structure was photographed with an optical microscope of 200 to 400 times, and the particle size was measured by a crossing method. Specifically, an average particle size was obtained by arbitrarily drawing a straight line on the photographed photo, and measuring the number of intersections of the length of the straight line and the grain boundary. The particle size was evaluated by changing the length and number of lines so that 50 to 100 particles could be counted.
(B) Identification of intermetallic compound, dimensions (particle diameter), and area ratio The wires of Examples and Comparative Examples were made into thin films by an electrolytic polishing thin film method (twin jet polishing method), and a transmission electron microscope (TEM) was used. An arbitrary range was observed at a magnification of 6000 to 30000 times. Next, using an energy dispersive X-ray detector (EDX), an electron beam was focused on the intermetallic compound, and Al—Fe, Al—Fe—Si, and Al—Zr intermetallic compounds were detected.
The size of the intermetallic compound was judged from the scale of the photographed photo, and the shape was calculated by converting it into an equivalent volume sphere. The area ratios a and b of the intermetallic compound are set based on the photographed images, and a range in which about 5 to 10 for the intermetallic compound A and 20 to 50 for the intermetallic compound B can be counted, The area of the intermetallic compound was calculated from the size and number of each intermetallic compound, and the area of each intermetallic compound was divided by the area of the range to be counted.
The area ratio is calculated by using the sample thickness of the thin piece as a reference thickness of 0.15 μm. If the sample thickness is different from the reference thickness, convert the sample thickness to the reference thickness, that is, by multiplying the area ratio calculated based on the photographed (reference thickness / sample thickness) The area ratio can be calculated. In this example and the comparative example, the sample thickness was calculated by observing the interval of the equal thickness stripes observed from the photograph, and was about 0.15 μm in all the samples.
(C) Tensile strength and tensile elongation at break Three pieces each were tested according to JIS Z 2241, and the average value was obtained.
(D) Conductivity In a constant temperature bath holding a test piece having a length of 300 mm at 20 ° C. (± 0.5 ° C.), three specific resistances were measured using the four probe method, and the average conductivity was measured. Calculated. The distance between the terminals was 200 mm.
(E) Number of repeated fractures As a standard for bending fatigue resistance, the strain amplitude at room temperature was ± 0.17%. Bending fatigue resistance varies with strain amplitude. When the strain amplitude is large, the fatigue life is shortened, and when the strain amplitude is small, the fatigue life is lengthened. Since the strain amplitude can be determined by the wire diameter of the wire rod 1 and the bending radii of the bending jigs 2 and 3 shown in FIG. 1, the wire diameter of the wire rod 1 and the bending radii of the bending jigs 2 and 3 are arbitrarily set and bent. It is possible to conduct a fatigue test.
By using a double-bending bending fatigue tester manufactured by Fujii Seiki Co., Ltd. (currently Fujii Co., Ltd.) and using a jig that gives a bending strain of ± 0.17% to the wire, repeated bending is performed. The number of return breaks was measured. The number of repeated ruptures was measured four by four and the average value was determined. As shown in the explanatory view of FIG. 1, the wire 1 was inserted with a gap of 1 mm between the bending jigs 2 and 3, and repeatedly moved in such a manner as to be along the jigs 2 and 3. One end of the wire was fixed to a holding jig 5 so that it could be bent repeatedly, and a weight 4 of about 10 g was hung from the other end. Since the holding jig 5 moves during the test, the wire 1 fixed to the holding jig 5 also moves and can be bent repeatedly. The repetition is performed under the condition of 1.5 Hz (1.5 reciprocations per second), and when the wire specimen 1 breaks, the weight 4 falls and stops counting.
If the number of times of opening and closing per day is 10 and the use for 10 years is assumed, the number of times of opening and closing is 36500 (calculated as 365 days a year). The actually used electric wire is not a single wire but has a stranded wire structure, and since the coating process is performed, the burden on the electric wire conductor becomes a fraction. The number of repeated fractures of 50000 times or more that can ensure sufficient bending fatigue resistance as an evaluation value for a single wire is preferred, and more preferably 70000 times or more.
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000002
Figure JPOXMLDOC01-appb-T000002
Figure JPOXMLDOC01-appb-T000003
Figure JPOXMLDOC01-appb-T000003
Figure JPOXMLDOC01-appb-T000004
Figure JPOXMLDOC01-appb-T000004
　表１－１、表１－２、表２－１及び表２－２の結果から以下のことが分かる。
　比較例１０１～１０３ではアルミニウム合金の添加成分が本発明の範囲外である。比較例１０１では、Ｆｅが少なすぎるため、金属間化合物ＡおよびＢが少なくなり、引張強度、繰返破断回数が悪い。比較例１０２では、Ｆｅが多すぎるため、金属間化合物ＡおよびＢが多くなり、繰返破断回数、導電率が悪い。比較例１０３では、Ｚｒが多すぎるため、金属間化合物Ｂが多くなり、繰返破断回数、導電率が悪い。
　比較例１０４～１１０及び比較例２０１は、アルミニウム合金導体中の金属間化合物の面積率が本発明の範囲外であるか、製造中に断線したものを示す。ここでは、アルミニウム合金の製造条件によって本発明の規定するアルミニウム合金導体が得られなかった例を示す。比較例１０４は、鋳造冷却速度が遅すぎたため、伸線加工中に断線した。比較例１０５は、鋳造冷却速度が速すぎて、金属間化合物Ａが少なく、金属間化合物Ｂが多くなり、繰返破断回数、導電率が悪い。比較例１０６～１０８は、それぞれ中間焼鈍の温度が高すぎたか低すぎたかあるいは時間が短すぎたために、いずれも伸線加工中に断線した。比較例１０９は、仕上げ焼鈍工程での軟化不足が原因で未焼鈍状態となり、金属間化合物が観察されなかったため、引張破断伸びが悪い。比較例１１０は、仕上げ焼鈍温度が高すぎたために、金属間化合物Ｂが少なく、引張強度、導電率、引張破断伸び、繰返破断回数が悪い。比較例２０１は仕上げ焼鈍をバッチ式焼鈍炉で行なったものであるが、金属間化合物Ｂが少なくなり、繰返破断回数が悪い。
　これに対し実施例１～１３では、引張強度、導電率、引張破断伸び（柔軟性）、繰返破断回数（耐屈曲疲労特性）に優れたアルミニウム合金導体が得られた。 The following can be understood from the results of Table 1-1, Table 1-2, Table 2-1, and Table 2-2.
In Comparative Examples 101 to 103, the additive component of the aluminum alloy is outside the scope of the present invention. In Comparative Example 101, since Fe is too small, intermetallic compounds A and B are reduced, and the tensile strength and the number of repeated fractures are poor. In Comparative Example 102, since there is too much Fe, intermetallic compounds A and B increase, and the number of repeated fractures and electrical conductivity are poor. In Comparative Example 103, since there is too much Zr, the intermetallic compound B increases, and the number of repeated fractures and the electrical conductivity are poor.
Comparative Examples 104 to 110 and Comparative Example 201 show that the area ratio of the intermetallic compound in the aluminum alloy conductor is out of the range of the present invention or is broken during the production. Here, an example is shown in which the aluminum alloy conductor defined by the present invention is not obtained depending on the production conditions of the aluminum alloy. In Comparative Example 104, the casting cooling rate was too slow, so the wire was broken during wire drawing. In Comparative Example 105, the casting cooling rate is too fast, the amount of intermetallic compound A is small, the amount of intermetallic compound B is large, and the number of repeated fractures and the electrical conductivity are poor. In Comparative Examples 106 to 108, the temperature of the intermediate annealing was too high or too low, or the time was too short. Comparative Example 109 is in an unannealed state due to insufficient softening in the final annealing step, and no intermetallic compound was observed, so that the tensile elongation at break was poor. In Comparative Example 110, since the finish annealing temperature was too high, the amount of intermetallic compound B was small, and the tensile strength, electrical conductivity, tensile elongation at break, and number of repeated fractures were poor. In Comparative Example 201, finish annealing was performed in a batch annealing furnace, but the amount of intermetallic compound B was reduced and the number of repeated fractures was poor.
On the other hand, in Examples 1 to 13, aluminum alloy conductors excellent in tensile strength, electrical conductivity, tensile breaking elongation (flexibility), and number of repeated breaking (flexural fatigue resistance) were obtained.
　本発明をその実施態様とともに説明したが、我々は特に指定しない限り我々の発明を説明のどの細部においても限定しようとするものではなく、添付の請求の範囲に示した発明の精神と範囲に反することなく幅広く解釈されるべきであると考える。 While this invention has been described in conjunction with its embodiments, we do not intend to limit our invention in any detail of the description unless otherwise specified and are contrary to the spirit and scope of the invention as set forth in the appended claims. I think it should be interpreted widely.
　本願は、２０１０年２月２６日に日本国で特許出願された特願２０１０－０４３４８９に基づく優先権を主張するものであり、これはここに参照してその内容を本明細書の記載の一部として取り込む。 This application claims priority based on Japanese Patent Application No. 2010-043489 filed in Japan on February 26, 2010, which is hereby incorporated herein by reference. Capture as part.
１　試験片（線材）
２、３　曲げ治具
４　重り
５　押さえ冶具 1 Test piece (wire)
2, 3 Bending jig 4 Weight 5 Holding jig

Claims (8)

  1. 　Ｆｅを０．４～０．９ｍａｓｓ％を含有し、残部Ａｌと不可避不純物からなるアルミニウム合金導体であって、
    前記導体中に２種類の金属間化合物Ａ、Ｂが存在し、
    前記金属間化合物Ａの粒子径は０．１μｍ以上２μｍ以下の範囲であり、
    前記金属間化合物Ｂの粒子径は０．０３μｍ以上０．１μｍ未満の範囲であり、
    前記導体中の任意の範囲における、前記金属間化合物Ａの面積率ａ、前記金属間化合物Ｂの面積率ｂが、それぞれ１％　≦　ａ　≦　６％、１％　≦　ｂ　≦　５％を満足することを特徴とするアルミニウム合金導体。     An aluminum alloy conductor containing 0.4 to 0.9 mass% of Fe, the balance being Al and inevitable impurities,
    Two types of intermetallic compounds A and B exist in the conductor,
    The particle size of the intermetallic compound A is in the range of 0.1 μm to 2 μm,
    The particle size of the intermetallic compound B is in the range of 0.03 μm or more and less than 0.1 μm,
    The area ratio a of the intermetallic compound A and the area ratio b of the intermetallic compound B in an arbitrary range in the conductor satisfy 1% ≦ a ≦ 6% and 1% ≦ b ≦ 5%, respectively. Aluminum alloy conductor characterized by
  2. 　Ｆｅを０．４～０．９ｍａｓｓ％と、Ｚｒを０．０１～０．４ｍａｓｓ％とを含有し、残部Ａｌと不可避不純物からなるアルミニウム合金導体であって、
    前記導体中に２種類の金属間化合物Ａ、Ｂが存在し、
    前記金属間化合物Ａの粒子径は０．１μｍ以上２μｍ以下の範囲であり、
    前記金属間化合物Ｂの粒子径は０．０３μｍ以上０．１μｍ未満の範囲であり、
    前記導体中の任意の範囲における、前記金属間化合物Ａの面積率ａ、前記金属間化合物Ｂの面積率ｂが、それぞれ１％　≦　ａ　≦　６％、１％　≦　ｂ　≦　７．５％を満足することを特徴とするアルミニウム合金導体。     An aluminum alloy conductor containing 0.4 to 0.9 mass% of Fe and 0.01 to 0.4 mass% of Zr, the balance being Al and inevitable impurities,
    Two types of intermetallic compounds A and B exist in the conductor,
    The particle size of the intermetallic compound A is in the range of 0.1 μm to 2 μm,
    The particle size of the intermetallic compound B is in the range of 0.03 μm or more and less than 0.1 μm,
    The area ratio a of the intermetallic compound A and the area ratio b of the intermetallic compound B in an arbitrary range in the conductor satisfy 1% ≦ a ≦ 6% and 1% ≦ b ≦ 7.5%, respectively. An aluminum alloy conductor characterized by:
  3. 　前記導体の製造工程の最後に急熱、急冷の工程を含む連続通電熱処理が施されることにより、伸線方向の垂直断面における結晶粒径が１～１５μmとなされる請求項１または請求項２に記載のアルミニウム合金導体。 3. The crystal grain size in a vertical section in the wire drawing direction is set to 1 to 15 μm by performing continuous energization heat treatment including rapid heating and rapid cooling processes at the end of the conductor manufacturing process. The aluminum alloy conductor described in 1.
  4. 　引張強度が８０ＭＰａ以上、及び導電率が６０％ＩＡＣＳ以上である請求項１～３のいずれか１項に記載のアルミニウム合金導体。 The aluminum alloy conductor according to any one of claims 1 to 3, having a tensile strength of 80 MPa or more and an electrical conductivity of 60% IACS or more.
  5. 　引張破断伸びが１０％以上である請求項１～４のいずれか１項に記載のアルミニウム合金導体。 The aluminum alloy conductor according to any one of claims 1 to 4, which has a tensile elongation at break of 10% or more.
  6. 　再結晶組織を有する請求項１～５のいずれか１項に記載のアルミニウム合金導体。 The aluminum alloy conductor according to any one of claims 1 to 5, which has a recrystallized structure.
  7. 　前記導体が移動体内で、バッテリーケーブル、ハーネス、またはモータ用線材として用いられることを特徴とする請求項１～６のいずれか１項に記載のアルミニウム合金導体。 The aluminum alloy conductor according to any one of claims 1 to 6, wherein the conductor is used as a battery cable, a harness, or a wire for a motor in a moving body.
  8. 　前記導体が車両、電車、または航空機に用いられることを特徴とする請求項１～７のいずれか１項に記載のアルミニウム合金導体。 The aluminum alloy conductor according to any one of claims 1 to 7, wherein the conductor is used in a vehicle, a train, or an aircraft.
PCT/JP2011/054399 2010-02-26 2011-02-25 Aluminum alloy conductor WO2011105586A1 (en)

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CN201180010674.4A CN102803531B (en) 2010-02-26 2011-02-25 Aluminium alloy conductor
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EP2754725A4 (en) * 2011-09-05 2015-06-17 Dyden Corp Aluminum-based electroconductive material, and electric wire and cable obtained using same
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JP2018070915A (en) * 2016-10-25 2018-05-10 矢崎総業株式会社 Aluminum single wire, aluminum wire and wire harness using the same

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EP2540850B1 (en) 2017-11-15
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CN102803531A (en) 2012-11-28
EP2540850A4 (en) 2013-11-06

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