WO2012133634A1 - アルミニウム合金導体 - Google Patents
アルミニウム合金導体 Download PDFInfo
- Publication number
- WO2012133634A1 WO2012133634A1 PCT/JP2012/058335 JP2012058335W WO2012133634A1 WO 2012133634 A1 WO2012133634 A1 WO 2012133634A1 JP 2012058335 W JP2012058335 W JP 2012058335W WO 2012133634 A1 WO2012133634 A1 WO 2012133634A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- wire
- aluminum alloy
- heat treatment
- wire drawing
- cross
- Prior art date
Links
Images
Classifications
-
- 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
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B5/00—Non-insulated conductors or conductive bodies characterised by their form
- H01B5/02—Single bars, rods, wires, or strips
Definitions
- the present invention relates to an aluminum alloy conductor used as a conductor of an electric wiring body.
- 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.
- wire harnesses are composed of several to several tens of metal wires that are twisted and covered with a coated wire.
- the strength of the metal wire can affect the strength of the wire.
- a low-strength metal wire that is easy for operators to handle. Due to the above problems and requirements, there is a demand for a conductive wire having high bending fatigue resistance even at low strength.
- flexibility is also required for handling properties, and in many cases, a blunt material (annealed material) that can secure an elongation of 10% or more, which is an evaluation index of flexibility, is used.
- the material is excellent in the appropriate proof stress that is easy to handle for the operator, the conductivity necessary for flowing a large amount of electricity, and the resistance to bending fatigue. Is required.
- the proof stress is a stress when a specified permanent elongation occurs after removing the force, and can be an index of strength when expressing workability.
- 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.
- the materials alloyed by adding various additive elements have a problem that the conductivity is lowered due to a solid solution phenomenon of the additive element in aluminum, and the handling property is poor because of high proof stress. Therefore, it is essential to limit and select the additive element and not to disconnect, to prevent a decrease in conductivity, and to appropriately control the proof stress and the bending fatigue resistance.
- Patent Documents 1 to 4 Representative examples of aluminum conductors used for electric wiring bodies of moving bodies include those described in Patent Documents 1 to 4. However, since the electric wire conductor described in Patent Document 1 has a large amount of Mg and Si, it may cause disconnection during wire drawing.
- the aluminum conductive wire specifically described in Patent Document 2 is not subjected to finish annealing. A higher flexibility is required for the mounting work on the vehicle body.
- Patent Document 3 discloses an aluminum conductive wire that is lightweight, flexible, and excellent in flexibility, but is difficult to handle because of its high strength.
- Patent Document 4 is a foil material. The form of deformation differs between the plate material and the foil material. This processing history affects the formation of the crystal texture in the subsequent process, and the way of forming the crystal orientation differs. Therefore, obtaining the desired crystal texture from the line is technically different from obtaining the desired crystal texture from the foil.
- An object of the present invention is to provide an aluminum alloy conductor that is excellent in electrical conductivity and bending fatigue resistance, and has an appropriate yield strength with good handling properties.
- the present inventors have made various studies and formed a crystal texture by controlling the manufacturing conditions such as heat treatment of aluminum alloy and the degree of processing before heat treatment, while maintaining excellent bending fatigue resistance and conductivity.
- the present inventors have found that an aluminum alloy conductor having a proof strength reduced to an appropriate range can be produced, and have reached the present invention based on this finding.
- the crystal grain size in the cross section perpendicular to the wire drawing direction having a crystal texture of 20% or more of the area ratio of the crystal grains having the (100) plane located parallel to the cross section perpendicular to the wire drawing direction of the wire
- An aluminum alloy conductor characterized by having a thickness of 1 to 30 ⁇ m.
- the aluminum alloy conductor according to (1) wherein the area ratio of crystal grains having a (100) plane located at is 20% or more.
- the alloy composition of the aluminum alloy conductor is Fe: 0.01-0.4 mass%, Mg: 0.04-0.3 mass%, Si: 0.02-0.3 mass%, Cu: The aluminum alloy conductor according to (1) or (2), comprising 0.1 to 0.5 mass% and comprising the balance Al and inevitable impurities.
- the aluminum alloy conductor of the present invention has an appropriate yield strength that is not too high, it is excellent in handling when the wire harness is mounted on a vehicle. Moreover, it is excellent in electrical conductivity and is useful as a battery cable, harness or motor lead wire mounted on a moving body. In particular, it can be suitably used for doors, trunks, bonnets and the like that are excellent in bending fatigue resistance and require extremely high bending fatigue resistance.
- FIG. 1 shows a range that is located within a radius of 2/3 from the center of a circle in a cross section perpendicular to the drawing direction of the wire, and that is 1/3 inward from the circumference in the cross section perpendicular to the drawing direction of the wire It is explanatory drawing which represents the range to be located typically.
- FIG. 2 is an explanatory diagram of a test for measuring the number of repeated fractures performed in the examples.
- the aluminum alloy conductor of the present invention can have excellent electrical conductivity, bending fatigue resistance, and appropriate proof stress by defining the crystal texture as follows.
- the crystal texture is defined using a crystal plane located parallel to a cross section perpendicular to the wire drawing direction of the wire.
- the crystal texture is a structure composed of polycrystalline grains in which a certain number of crystal orientations are gathered.
- the crystal texture of the aluminum alloy conductor of the present invention is a crystal texture in which the area ratio of crystal grains having a (100) plane located parallel to the cross section perpendicular to the wire drawing direction is 20% or more. More preferably, in a range (center portion) located within a radius of 2/3 from the center of the circle in the cross section perpendicular to the wire drawing direction, the wire is positioned parallel to the cross section perpendicular to the wire drawing direction (100).
- the area ratio of crystal grains having a plane is 20% or more (the upper limit is not limited, but 50% or less is preferable), and 1 in the radial direction from the circumference in the cross section perpendicular to the wire drawing direction. / 3 In the range located on the inner side (outer peripheral part), the area ratio of crystal grains having a (100) plane located parallel to the cross section perpendicular to the wire drawing direction is 20% or more (the upper limit is limited) However, it is preferably 50% or less).
- the center part and the circumferential part are schematically shown in FIG. FIG.
- the area ratio of the crystal grains is 20% or more.
- the (100) plane can improve the bending fatigue resistance when the wire is bent as shown in FIG. 2 with respect to the wire drawing direction.
- the area ratio of crystal orientation is a value measured by the EBSD method.
- the EBSD method is an abbreviation for Electron BackScatter Diffraction, and is a crystal orientation analysis technique using reflected electron Kikuchi line diffraction that occurs when a sample is irradiated with an electron beam in a scanning electron microscope (SEM).
- the area ratio is the ratio of the area of crystal grains tilted within ⁇ 15 ° from an ideal crystal plane such as the (100) plane in the wire drawing direction to the total measured area.
- the information obtained in the azimuth analysis by EBSD includes azimuth information up to a depth of several tens of nanometers at which the electron beam penetrates the sample, but is sufficiently small with respect to the measured width. Let us treat it as an area ratio.
- the crystal grain size in the cross section perpendicular to the drawing direction of the aluminum wire is 1-30 ⁇ m. If the crystal grain size is too small, the partially recrystallized structure remains and the desired crystal texture cannot be obtained, and the elongation is significantly reduced. When a coarse structure having a crystal grain size that is too large is formed, the deformation behavior becomes non-uniform, and the elongation is lowered and the proof stress is remarkably lowered as in the case where the crystal grain size is too small.
- the crystal grain size is preferably 5 to 30 ⁇ m, more preferably 5 to 20 ⁇ m.
- the “crystal grain size” in the present invention is an average grain size obtained by observing with an optical microscope and measuring the grain size by a crossing method, and is an average value of 50 to 100 crystal grains.
- the alloy composition is set as described below, and the manufacturing conditions such as heat treatment and degree of processing before heat treatment are controlled as follows. This can be achieved. Examples of preferred production methods and alloy compositions are described below, but are examples for understanding the invention, and the wire diameter and the like are not limited thereto.
- the aluminum alloy conductor of the present invention comprises: [1] melting, [2] casting, [3] hot or cold working, [4] first wire drawing, [5] intermediate heat treatment, [6] second wire drawing. It can be manufactured through each step of processing and [7] final heat treatment (finish annealing).
- the degree of processing is preferably 1 or more and 6 or less.
- the cold-drawn workpiece is subjected to an intermediate heat treatment.
- the target crystal texture is a state in which crystal grains having a (100) plane located parallel to a cross section perpendicular to the wire drawing direction are uniformly dispersed.
- the intermediate heat treatment temperature is 230 to 290 ° C. When the intermediate heat treatment temperature is less than 230 ° C., non-recrystallized grains remain and the desired crystal texture cannot be obtained. If the temperature exceeds 290 ° C., the crystal orientation rotates during recrystallization, and the desired crystal texture cannot be obtained.
- the intermediate heat treatment temperature is preferably 240 ° C. to 280 ° C.
- the intermediate heat treatment time is 1 to 10 hours.
- the intermediate heat treatment time is less than 1 hour, unrecrystallized grains remain, and the desired recrystallized grain structure cannot be obtained. If it exceeds 10 hours, the crystal orientation rotates during recrystallization depending on the temperature, so that the target crystal texture cannot be obtained.
- the intermediate heat treatment time is preferably 2 to 8 hours.
- the processing rate at this time is 10 to 30%.
- the processing rate is given as 100 times the difference in cross-sectional area before and after wire drawing divided by the original cross-sectional area.
- the processing rate is less than 10%, the applied strain is insufficient, and the target crystal texture cannot be obtained during the heat treatment in the next step. If it exceeds 30%, the recrystallization rate of the (100) plane located parallel to the cross section perpendicular to the drawing direction becomes low, and the desired crystal texture cannot be obtained.
- the processing rate is preferably 15% to 25%.
- Final heat treatment finish annealing
- the cold-drawn workpiece is subjected to final heat treatment by continuous heat treatment.
- the final heat treatment can be performed by one of two methods: continuous energization heat treatment and continuous running heat treatment.
- the continuous energization heat treatment is performed by annealing with Joule heat generated from itself by passing an electric current through a wire passing through two electrode wheels. It includes the steps of rapid heating and quenching, and the wire can be annealed by controlling the wire temperature and annealing time. Cooling is performed by passing the wire continuously in water or a nitrogen gas atmosphere after rapid heating. If one or both of the wire temperature and the annealing time are too low, the required flexibility for in-vehicle mounting cannot be obtained, and if it is too high, the crystal orientation will rotate excessively due to over-annealing, and the target crystal assembly The organization cannot be obtained. Furthermore, the bending fatigue resistance is also deteriorated.
- this expression expresses the range in which the texture can be obtained.
- the current value and voltage value are actually controlled, but the adjustment varies depending on the equipment environment, etc., and the current value and voltage value are uniquely defined. Not determined.
- the wire temperature y (° C.) represents the temperature immediately before passing through the cooling step, at which the temperature of the wire becomes the highest. y (° C.) is usually in the range of 414 to 620 (° C.).
- the wire is continuously passed through an annealing furnace kept at a high temperature and annealed. It includes the steps of rapid heating and rapid cooling, and the wire can be annealed under the control of the annealing furnace temperature and annealing time. Cooling is performed by passing the wire continuously in water or a nitrogen gas atmosphere after rapid heating. If one or both of the annealing furnace temperature and the annealing time are too low, the required flexibility for vehicle mounting cannot be obtained, and if it is too high, the crystal orientation will rotate excessively due to over-annealing, and the target crystal A texture cannot be obtained. Furthermore, the bending fatigue resistance is also deteriorated.
- the annealing furnace temperature is z (° C.) and the annealing time is x (seconds)
- z (° C.) is usually in the range of 300 to 596 (° C.).
- the finish annealing may be induction heating in which a wire continuously passes through a magnetic field and is annealed.
- the preferred component constitution of the present invention is as follows: Fe is 0.01 to 0.4 mass%, Mg is 0.04 to 0.3 mass%, Si is 0.02 to 0.3 mass%, and Cu is 0.1 to It contains 0.5 mass% and consists of the balance Al and inevitable impurities.
- the reason why the Fe content is set to 0.01 to 0.4 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, Al-Fe-Si, Al-Fe-Si-Mg, Al-Fe-Cu-Si. This crystallized substance or precipitate acts as a crystal grain refiner and improves the 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, and the desired bending fatigue resistance cannot be obtained. Moreover, it will be in a supersaturated solid solution state and electrical conductivity will also fall.
- the Fe content is preferably 0.15 to 0.3 mass%, more preferably 0.18 to 0.25 mass%.
- the Mg content is set to 0.04 to 0.3 mass% because Mg dissolves in the aluminum base material, and a part thereof forms precipitates with Si to form bending fatigue resistance and heat resistance. It is because it can improve. If the Mg content is too low, the effect is insufficient, and if it is too high, the conductivity is lowered. Moreover, when there is much content of Mg, yield strength will become excess, a moldability and twist property will deteriorate, and workability will worsen.
- the Mg content is preferably 0.08 to 0.3 mass%, more preferably 0.10 to 0.28 mass%.
- the reason why the Si content is 0.02 to 0.3 mass% is that, as described above, Si forms a compound with Mg and exhibits a function of improving bending fatigue resistance and heat resistance. If the Si content is too low, the effect is insufficient, and if it is too high, the conductivity decreases.
- the Si content is preferably 0.04 to 0.25 mass%, more preferably 0.10 to 0.25 mass%.
- the Cu content is 0.1 to 0.5 mass%, Cu is dissolved in the aluminum base material, which contributes to improvement in bending fatigue resistance, creep resistance, and heat resistance. If the Cu content is too low, the effect is insufficient, and if it is too high, the corrosion resistance and the conductivity are lowered.
- the Cu content is preferably 0.20 to 0.45 mass%, more preferably 0.25 to 0.40 mass%.
- Inevitable impurities in the alloy composition include normal ones, and examples thereof include Ni, Ti, Ga, B, Zn, Cr, Mn, and Zr.
- the aluminum alloy conductor of the present invention is preferably 0.15 to 1.2 mm in diameter and more preferably 0.30 to 0.55 mm in diameter.
- the aluminum alloy wire of the present invention preferably has a 0.2% proof stress of 35 to 80 MPa in a tensile test measured in the longitudinal direction of the conductor. If it is less than 35 MPa, the proof stress is too low to withstand an unexpected impact such as when the harness is attached, and there is a risk of disconnection. If it exceeds 80 MPa, the handling property is difficult.
- a more preferable range of the 0.2% proof stress is 35 to 70 MPa, more preferably 35 to 60 MPa.
- the 0.2% yield strength is the yield strength against permanent elongation of 0.2% calculated by the offset method.
- the aluminum alloy conductor of the present invention has the above-mentioned moderate proof stress, excellent electrical conductivity, and flexibility, so that it has excellent handling properties during work and is wired in a limited space as described above. It is suitable for electric wiring of a moving body. Moreover, since it has excellent bending fatigue resistance, it can be suitably used for repeated opening / closing parts such as doors.
- Example 1 Comparative Example 1, Conventional Example 1 Rolling is carried out while continuously casting the molten metal in a water-cooled mold so that Fe, Mg, Si, Cu, and Al are in the amounts shown in Table 1 (mass%).
- the bar was about 10 mm ⁇ .
- the casting cooling rate at this time is 1 to 20 ° C./second.
- the surface was peeled to obtain about 9.5 mm ⁇ , which was drawn to 2.6 mm ⁇ and softened at a temperature of 350 to 400 ° C. for 2 to 3 hours.
- the drawing history and heat treatment so far can be expressed as follows. 9.5mm ⁇ ⁇ 2.6mm ⁇ ⁇ softening treatment
- wire drawing was performed at a processing rate of 10 to 30% (processing rate of about 9% and about 31).
- the drawing history and heat treatment so far can be expressed as follows. ⁇ 0.330mm ⁇ ⁇ intermediate heat treatment ⁇ 0.315mm ⁇ (working rate approx. 9%) ⁇ 0.340mm ⁇ ⁇ intermediate heat treatment ⁇ 0.315mm ⁇ (working rate approx. 14%) ⁇ 0.350mm ⁇ ⁇ intermediate heat treatment ⁇ 0.315mm ⁇ (working rate approx. 19%) ⁇ 0.360mm ⁇ ⁇ Intermediate heat treatment ⁇ 0.315mm ⁇ (Processing rate approx.
- continuous energization heat treatment was performed at a temperature of 426 to 605 ° C. for a time of 0.03 to 0.54 seconds, and continuous running heat treatment was performed at a temperature of 328 to 559 ° C. for a time of 1.5 It was performed under a condition of ⁇ 5.0 seconds.
- the temperature is a fiber type radiation thermometer (manufactured by Japan Sensor Co., Ltd.), the wire temperature y (° C.) immediately before passing through the water where the temperature of the wire becomes the highest (during continuous energization heat treatment), or the annealing furnace temperature z (° C.) ( During continuous running heat treatment).
- batch-type heat treatment was performed under the conditions of a heat treatment furnace temperature of 400 ° C. and a time of 3600 seconds.
- (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.
- the EBSD method was used for the analysis of the crystal orientation in the present invention.
- a sample area mainly having a diameter of 300 ⁇ m was scanned in 0.5 ⁇ m steps, and the orientation was analyzed.
- the measurement area and scan step are adjusted for each sample, the measurement area is set so that 25 or more crystal grains are included, and the scan step is set to about 1/10 or less of the average crystal grain size of the sample. did.
- the analysis was performed such that the total of the plurality of sheets was 25 or more.
- the area ratio of crystal orientation is the ratio of the area of crystal grains tilted within a range of ⁇ 15 ° from an ideal crystal plane such as the (100) plane located parallel to the cross section perpendicular to the wire drawing direction to the total measured area. is there.
- Table 2 the measurement range of the (100) area ratio of the whole, the central portion, and the outer peripheral portion is set in each, and the measurement range of the entire (100) area ratio is set so that the central portion and the outer peripheral portion are not biased. The measurement area was taken about 50% from the region.
- the yield strength was calculated by the offset method, and a value for permanent elongation of 0.2% (referred to as 0.2% yield strength) was used. For the flexibility, the tensile elongation at break was 10% or more.
- D Conductivity
- EC Three specific resistances were measured using a four-terminal method in a constant temperature bath holding a 300 mm long test piece at 20 ° C. ( ⁇ 0.5 ° C.), and the average conductivity was calculated. The distance between the terminals was 200 mm. The electrical conductivity passed 57% IACS or more.
- 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 curvature radii of the bending jigs 2 and 3 shown in FIG. 2, 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. The number of repeated ruptures by repeatedly bending using a jig that gives a bending strain of 0.17% using a double-bending bending fatigue tester manufactured by Fujii Seiki Co., Ltd. (currently Fujii Co., Ltd.) was measured.
- the number of repeated ruptures was measured four by four and the average value was determined.
- 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 thereto also moves and can be bent repeatedly.
- the repetition is performed under the condition of 100 reciprocations per minute, and when the wire specimen 1 breaks, the weight 4 falls and stops counting.
- the number of repeated breaks is counted as one round trip.
- the number of repeated breaks was 60000 times or more.
- the number of repeated breaks was standardized by 0.2% proof stress. A value obtained by dividing the number of repeated fractures by 0.2% proof stress was 1.5 ⁇ 10 3 times / MPa or more was regarded as acceptable.
- Each sample of Example 1 has an area ratio of crystal grains having a (100) plane positioned parallel to the cross section perpendicular to the wire drawing direction of the wire rod, and is (100) in the central portion and the outer peripheral portion. ) The area ratio of the surface was also 20% or more. In each sample of Example 2, the area ratio of the crystal grains having the (100) plane located parallel to the cross section perpendicular to the wire drawing direction is 20% or more, but either the central portion or the outer peripheral portion. In (100), the area ratio of the (100) plane was less than 20%. In each sample of Comparative Example 1 and the sample of Conventional Example 1, the area ratio of crystal grains having a (100) plane located parallel to the cross section perpendicular to the wire drawing direction of the wire was less than 20%.
- each sample of Comparative Example 1 and the sample of Conventional Example 1 are inferior in any of the characteristics, each sample of Example 1 and each sample of Example 2 have proof stress, electrical conductivity, tensile elongation at break, repetition rate. All of the number of return breaks had sufficient characteristics.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Conductive Materials (AREA)
- Non-Insulated Conductors (AREA)
- Metal Extraction Processes (AREA)
Abstract
Description
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線材に純銅の導体線材と同じ電流を流すためには、純アルミニウムの導体線材の断面積を純銅の導体線材の約1.5倍にする必要があるが、それでも質量では銅に比べて約半分となるので、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。
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線材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、過度な力を必要としないためにも強度は高すぎない方が良い。ワイヤーハーネスはその複雑な回路構成のため、ワイヤーハーネスに付属しているコネクタ同士をつなげたり、ワイヤーハーネスを所定の回路に合うように曲げたりするなど人の手によって組み立てている。そのような状況下で、電線の強度が高いとワイヤーハーネスを曲げたり持ち上げたりする際に、過大な力が必要であるため、1日に何時間も作業を繰り返す作業者にとって非常につらい作業となり、作業性が劣ることが予想される。一般に、ワイヤーハーネスを構成するものとしては、金属線を数本~数十本束ねて撚線とし、更に被覆を施した電線を取り扱うが、金属線の強度は電線の強度に影響を及ぼすことが知られている。よって、作業者の取り回しがしやすい、低強度金属線の開発が要求されている。
以上のような課題、要求により低強度においても耐屈曲疲労特性が高い導電線が求められている。また、取り回し性には柔軟性も求められており、柔軟性の評価指標である伸びが10%以上確保できる鈍し材(焼鈍材)が使われていることが多い。
(1)線材の伸線方向に垂直な断面に平行に位置する(100)面を有する結晶粒の面積率が20%以上の結晶集合組織を持ち、伸線方向に垂直な断面における結晶粒径が1~30μmであることを特徴とするアルミニウム合金導体。
(2)線材の伸線方向に垂直な断面における円の中心から2/3の半径内に位置する範囲において、線材の伸線方向に垂直な断面に平行に位置する(100)面を有する結晶粒の面積率が20%以上であり、かつ、線材の伸線方向に垂直な断面における円周から半径方向に1/3内側に位置する範囲において、線材の伸線方向に垂直な断面に平行に位置する(100)面を有する結晶粒の面積率が20%以上であることを特徴とする(1)に記載のアルミニウム合金導体。
(3)前記アルミニウム合金導体の合金組成が、Fe:0.01~0.4mass%と、Mg:0.04~0.3mass%と、Si:0.02~0.3mass%と、Cu:0.1~0.5mass%とを含有し、残部Alと不可避不純物からなる(1)または(2)に記載のアルミニウム合金導体。
(4)導体の長手方向で測定した引張試験において0.2%耐力が35~80MPaであることを特徴とする(1)~(3)のいずれか1項に記載のアルミニウム合金導体。
(5)移動体内のバッテリーケーブル、ハーネス、またはモータ用導線として用いられることを特徴とする(1)~(4)のいずれか1項に記載のアルミニウム合金導体。
(6)前記移動体が自動車、電車、または航空機であることを特徴とする(5)に記載のアルミニウム合金導体。
(7)溶解、鋳造、熱間又は冷間加工を経て荒引線を形成した後、第1伸線加工、中間熱処理、第2伸線加工、最終熱処理の工程を有するアルミニウム合金の製造方法であって、中間熱処理を温度230~290℃で1~10時間、第2伸線加工の加工率を10~30%で行なう(1)~(6)記載のアルミニウム合金線の製造方法。
(8)前記最終熱処理が連続通電熱処理であり、下記式を満たす(7)記載のアルミニウム合金線の製造方法。
0.03≦x≦0.55、かつ
26x-0.6+377≦y≦23.5x-0.6+423(左辺と右辺のxは同値を代入)
(式中xは焼鈍時間(秒)を、yは線材温度(℃)を示す。)
(9)前記最終熱処理が連続送間熱処理であり、下記式を満たす(7)記載のアルミニウム合金線の製造方法。
1.5≦x≦5、かつ
-50x+550≦z≦-36x+650(左辺と右辺のxは同値を代入)
(式中xは焼鈍時間(秒)を、zは焼鈍炉温度(℃)を示す。)
本発明では線材の伸線方向に垂直な断面に平行に位置する結晶面を用いて結晶集合組織を規定する。結晶集合組織とは、ある一定の結晶方位が多く集合した多結晶粒で構成される組織のことである。本発明のアルミニウム合金導体の結晶集合組織は、線材の伸線方向に垂直な断面に平行に位置する(100)面を有する結晶粒の面積率が20%以上の結晶集合組織である。更に好ましくは、線材の伸線方向に垂直な断面における円の中心から2/3の半径内に位置する範囲(中心部)において、線材の伸線方向に垂直な断面に平行に位置する(100)面を有する結晶粒の面積率が20%以上であり(上限は制限するものではないが50%以下が好ましい)、かつ、線材の伸線方向に垂直な断面における円周から半径方向に1/3内側に位置する範囲(外周部)において、線材の伸線方向に垂直な断面に平行に位置する(100)面を有する結晶粒の面積率が20%以上である(上限は制限するものではないが50%以下が好ましい)結晶集合組織である。上記中心部と円周部を図1に模式的に示した。図1は線材の伸線方向に垂直な方向の断面図であってrは半径を示し、Aで示す部分が中心部であり、Bで示す部分が外周部である。このように領域を分けた理由のひとつは、線材の加工では、線材の中心部と外周部で変形の仕方が異なるが、異なる変形をした線材の中心部と外周部において、(100)面を有する結晶粒の面積率が、どちらも20%以上であるということ示すためである。このような結晶集合組織とすることにより、伸線方向に対して線材を図2のように屈曲させた際に、(100)面が耐屈曲疲労特性を向上させることができる。
なお、本発明における結晶方位の面積率はEBSD法によって測定した値とする。EBSD法とは、Electron BackScatter Diffractionの略で、走査電子顕微鏡(SEM)内で試料に電子線を照射したときに生じる反射電子菊池線回折を利用した結晶方位解析技術のことである。面積率は、伸線方向に(100)面などの理想結晶面から±15°以内の範囲で傾いている結晶粒の面積の全測定面積に対する割合である。EBSDによる方位解析において得られる情報は、電子線が試料に侵入する数十nmの深さまでの方位情報を含んでいるが、測定している広さに対して充分に小さいため、本明細書中では面積率として扱う。
本発明ではアルミニウム線材の伸線方向に垂直な断面における結晶粒径を1~30μmとする。結晶粒径が小さすぎると、部分再結晶組織が残存して目的の結晶集合組織が得られないばかりか、伸びが著しく低下する。結晶粒径の大きすぎる粗大な組織を形成すると変形挙動が不均一となり、結晶粒径が小さすぎるときと同様に伸びが低下するうえ、耐力が著しく低下する。結晶粒径は、好ましくは5~30μm、更に好ましくは5~20μmである。
なお、本発明における「結晶粒径」は光学顕微鏡により観察して交差法により粒径測定を行った平均粒径であり、50~100個の結晶粒の平均値とする。
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、[4]第1伸線加工、[5]中間熱処理、[6]第2伸線加工、[7]最終熱処理(仕上げ焼鈍)の各工程を経て製造することができる。
溶解は、後述するアルミニウム合金組成のそれぞれの実施態様の濃度となるような分量で溶製する。
次いで、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1~20℃/秒である。鋳造及び熱間圧延は、ビレット鋳造、押出法、及び金型法などにより行なってもよい。
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。加工度は、1以上6以下が好ましい。ここで加工度ηは、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。このときの加工度が小さすぎると、次工程の熱処理時、再結晶粒が粗大化し耐力及び伸びが著しく低下し、断線の原因にもなることがある。大きすぎると、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を生ずることがある。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、適宜この皮むきは省くこともできる。最終線径までの加工度が6以上になると予想される場合は、伸線加工中の断線を防止するため、適宜途中で軟化処理を行う。
次に、目的の結晶集合組織を得るために、冷間伸線した加工材に中間熱処理を施す。ここで、目的とする結晶集合組織とは、線材の伸線方向に垂直な断面に平行に位置する(100)面を有する結晶粒が均一に分散している状態である。中間熱処理温度は230~290℃である。中間熱処理温度が230℃未満であると、未再結晶粒が残存し、目的の結晶集合組織が得られない。290℃を越えると、再結晶中に結晶方位が回転してしまうため、目的の結晶集合組織が得られない。中間熱処理温度は好ましくは240℃~280℃である。中間熱処理時間は1~10時間である。中間熱処理時間が1時間未満であると、未再結晶粒が残存し、目的の再結晶粒号組織が得られない。10時間を越えると、温度によっては再結晶中に結晶方位が回転してしまうため、目的の結晶集合組織が得られない。中間熱処理時間は好ましくは2~8時間である。
さらに伸線加工を施す。このときの加工率は10~30%とする。ここで、加工率とは伸線加工前後の断面積の差を元の断面積で割って100をかけたものとして与えられる。加工率が10%未満であると、付与ひずみが不足し、次工程の熱処理時に目的の結晶集合組織が得られない。30%を越えると、伸線方向に垂直な断面に平行に位置する(100)面の再結晶率が低くなり、目的の結晶集合組織が得られない。加工率は好ましくは15%~25%である。
冷間伸線した加工材に連続熱処理により最終熱処理を行なう。最終熱処理は連続通電熱処理、連続走間熱処理の2つの方法のいずれかで行うことができる。
連続通電熱処理においては線材温度をy(℃)、焼鈍時間をx(秒)とすると、
0.03≦x≦0.55、かつ
26x-0.6+377≦y≦23.5x-0.6+423(左辺と右辺のxは同値を代入)
を満たすように行う。
上記式は温度と時間を制御することで再結晶させることを示すものである。温度が高いときは時間は短くてすむが、温度が比較的低温だと長時間の熱処理が必要になる。再結晶に適切な温度と時間を数式化したものである。また同時にこの式は集合組織が得られる範囲も表現している。
上記式の条件を満たすようにするには、実際には電流値、電圧値の制御をすることになるが、その調節は設備環境等によって異なり、電流値、電圧値の数値は一義的には定まらない。
なお、線材温度y(℃)は、線材として温度が最も高くなる、冷却工程に通過する直前の温度を表す。y(℃)は通常414~620(℃)の範囲内である。
連続走間熱処理においては焼鈍炉温度をz(℃)、焼鈍時間をx(秒)とすると、
1.5≦x≦5、かつ
-50x+550≦z≦-36x+650(左辺と右辺のxは同値を代入)
を満たすように行う。
これらの式も上記と同様に再結晶に適切で集合組織の得られる温度と時間を表現したもので、電流値、電圧値を設備環境に応じて調節してその関係を満たすようにできる。
z(℃)は通常300~596(℃)の範囲内である。
また、仕上げ焼鈍は上記2つの方法の他に、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。
本発明の好ましい成分構成は、Feを0.01~0.4mass%と、Mgを0.04~0.3mass%と、Siを0.02~0.3mass%と、Cuを0.1~0.5mass%とを含有し、残部Alと不可避不純物からなる。
合金組成中の不可避不純物は、通常のものがあり、例えば、Ni、Ti、Ga、B、Zn、Cr、Mn、Zrなどがあげられる。
本発明のアルミニウム合金線材は、導体の長手方向で測定した引張試験において0.2%耐力が35~80MPaを満たすものであることが好ましい。35MPa未満では、耐力が低すぎてハーネス取り付け時等の不意の衝撃などに耐えることができず、断線の恐れがある。80MPa超では、取り回し性に難がある。0.2%耐力のより好ましい範囲は、35~70MPa、更に好ましくは35~60MPaである。なお、0.2%耐力とは、オフセット法により算出した0.2%の永久伸びに対する耐力のことである。
上述したように本発明のアルミニウム合金導体は、上記の、適度な耐力と優れた導電率、柔軟性を有するため、作業中の取り回し性に優れ、限られたスペースに配線する前記のような各種移動体の電気配線に好適である。また、優れた耐屈曲疲労特性を有するため、ドアなどの繰り返し開閉部に好適に使用されうる。
Fe、Mg、Si、Cu、及びAlが表1に示す量(mass%)になるように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℃/秒である。
次いで、表面の皮むきを実施して、約9.5mmφとし、これを2.6mmφまで伸線加工し温度350~400℃で2~3時間の軟化処理を行った。ここまでの伸線加工履歴と熱処理は次のように表せる。
9.5mmφ→2.6mmφ→軟化処理
→0.330mmφ→中間熱処理→0.315mmφ(加工率約9%)
→0.340mmφ→中間熱処理→0.315mmφ(加工率約14%)
→0.350mmφ→中間熱処理→0.315mmφ(加工率約19%)
→0.360mmφ→中間熱処理→0.315mmφ(加工率約23%)
→0.370mmφ→中間熱処理→0.315mmφ(加工率約28%)
→0.380mmφ→中間熱処理→0.315mmφ(加工率約31%)
→0.370mmφ→中間熱処理→0.340mmφ(加工率約16%)
→0.375mmφ→中間熱処理→0.340mmφ(加工率約20%)
→0.410mmφ→中間熱処理→0.370mmφ(加工率約19%)
なお、線径の公差は±0.003以内に収めることができる。
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。
本発明における結晶方位の解析には、EBSD法を用いた。線材の伸線方向に垂直な断面において、主に直径300μmの試料面積に対し、0.5μmステップでスキャンし、方位を解析した。測定面積及びスキャンステップは試料毎に調整を行い、測定面積は結晶粒が25個以上含まれるように範囲を設定し、スキャンステップは試料の平均結晶粒の大きさの約1/10以下に設定した。結晶粒が大きすぎて解析像1枚で25個以上数えられない場合は、複数枚の合計で25個以上になるようにして解析した。結晶方位の面積率は、伸線方向に垂直な断面に平行に位置する(100)面などの理想結晶面から±15°以内の範囲で傾いている結晶粒の面積の全測定面積に対する割合である。なお、表2で全体、中心部、外周部の(100)面積率の測定範囲はそれぞれにおいて設定し、全体の(100)面積率の測定範囲は中心部と外周部が偏らないように、それぞれの領域から約50%ずつ測定面積をとった。
(c)耐力(0.2%耐力)及び柔軟性(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。耐力はオフセット法により算出し、0.2%の永久伸びに対する値(0.2%耐力と言う)を使用した。柔軟性は引張破断伸びが10%以上を合格とした。
(d)導電率(EC)
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。導電率は57%IACS以上を合格とした。
(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2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、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2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。繰り返しは往復100回/分の条件で行い、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。なお繰返破断回数は往復を1回としてカウントする。
繰返破断回数は、60000回以上を合格とした。また、繰返破断回数は0.2%耐力によって規格化を行った。繰返破断回数を0.2%耐力で割った値が1.5×103回/MPa以上であるものを合格とした。
比較例1の各試料及び従来例1の試料は、いずれかの特性で劣っているのに対し、実施例1の各試料、実施例2の各試料は耐力、導電率、引張破断伸び、繰返破断回数のすべてで十分な特性を有していた。
2、3 曲げ治具
4 重り
5 押さえ冶具
Claims (9)
- 線材の伸線方向に垂直な断面に平行に位置する(100)面を有する結晶粒の面積率が20%以上の結晶集合組織を持ち、伸線方向に垂直な断面における結晶粒径が1~30μmであることを特徴とするアルミニウム合金導体。
- 線材の伸線方向に垂直な断面における円の中心から2/3の半径内に位置する範囲において、線材の伸線方向に垂直な断面に平行に位置する(100)面を有する結晶粒の面積率が20%以上であり、かつ、線材の伸線方向に垂直な断面における円周から半径方向に1/3内側に位置する範囲において、線材の伸線方向に垂直な断面に平行に位置する(100)面を有する結晶粒の面積率が20%以上であることを特徴とする請求項1に記載のアルミニウム合金導体。
- 前記アルミニウム合金導体の合金組成が、Fe:0.01~0.4mass%と、Mg:0.04~0.3mass%と、Si:0.02~0.3mass%と、Cu:0.1~0.5mass%とを含有し、残部Alと不可避不純物からなる請求項1または2に記載のアルミニウム合金導体。
- 導体の長手方向で測定した引張試験において0.2%耐力が35~80MPaであることを特徴とする請求項1~3のいずれか1項に記載のアルミニウム合金導体。
- 移動体内のバッテリーケーブル、ハーネス、またはモータ用導線として用いられることを特徴とする請求項1~4のいずれか1項に記載のアルミニウム合金導体。
- 前記移動体が自動車、電車、または航空機であることを特徴とする請求項5に記載のアルミニウム合金導体。
- 溶解、鋳造、熱間又は冷間加工を経て荒引線を形成した後、第1伸線加工、中間熱処理、第2伸線加工、最終熱処理の工程を有するアルミニウム合金の製造方法であって、中間熱処理を温度230~290℃で1~10時間、第2伸線加工の加工率を10~30%で行なう請求項1~6記載のアルミニウム合金線の製造方法。
- 前記最終熱処理が連続通電熱処理であり、下記式を満たす請求項7記載のアルミニウム合金線の製造方法。
0.03≦x≦0.55、かつ
26x-0.6+377≦y≦23.5x-0.6+423(左辺と右辺のxは同値を代入)
(式中xは焼鈍時間(秒)を、yは線材温度(℃)を示す。) - 前記最終熱処理が連続送間熱処理であり、下記式を満たす請求項7記載のアルミニウム合金線の製造方法。
1.5≦x≦5、かつ
-50x+550≦z≦-36x+650(左辺と右辺のxは同値を代入)
(式中xは焼鈍時間(秒)を、zは焼鈍炉温度(℃)を示す。)
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2012527143A JP5184719B2 (ja) | 2011-03-31 | 2012-03-29 | アルミニウム合金導体 |
CN201280016455.1A CN103492597B (zh) | 2011-03-31 | 2012-03-29 | 铝合金导体 |
EP12763805.4A EP2692880B1 (en) | 2011-03-31 | 2012-03-29 | Aluminum alloy conductor |
US14/037,869 US20140020796A1 (en) | 2011-03-31 | 2013-09-26 | Aluminum alloy conductor |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2011-080344 | 2011-03-31 | ||
JP2011080344 | 2011-03-31 |
Related Child Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US14/037,869 Continuation US20140020796A1 (en) | 2011-03-31 | 2013-09-26 | Aluminum alloy conductor |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2012133634A1 true WO2012133634A1 (ja) | 2012-10-04 |
Family
ID=46931336
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2012/058335 WO2012133634A1 (ja) | 2011-03-31 | 2012-03-29 | アルミニウム合金導体 |
Country Status (5)
Country | Link |
---|---|
US (1) | US20140020796A1 (ja) |
EP (1) | EP2692880B1 (ja) |
JP (1) | JP5184719B2 (ja) |
CN (1) | CN103492597B (ja) |
WO (1) | WO2012133634A1 (ja) |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN104217784A (zh) * | 2013-05-28 | 2014-12-17 | 尼克桑斯公司 | 电导线及其制造方法 |
CN104781431A (zh) * | 2013-03-29 | 2015-07-15 | 古河电器工业株式会社 | 铝合金导体、铝合金绞线、被覆电线、线束以及铝合金导体的制造方法 |
WO2016047617A1 (ja) * | 2014-09-22 | 2016-03-31 | 古河電気工業株式会社 | アルミニウム合金線材、アルミニウム合金撚線、被覆電線、ワイヤーハーネスおよびアルミニウム合金線材の製造方法 |
EP2896706A4 (en) * | 2013-03-29 | 2016-08-03 | Furukawa Electric Co Ltd | ALUMINUM ALLOY DRIVER, ALUMINUM ALLOY TWISTED WIRE, COATED ELECTRICAL WIRE, WIRE HARNESS, AND PRODUCTION METHOD FOR ALUMINUM ALLOY DRIVERS |
US9650706B2 (en) | 2013-03-29 | 2017-05-16 | Furukawa Electric Co., Ltd. | Aluminum alloy wire rod, aluminum alloy stranded wire, coated wire, wire harness and manufacturing method of aluminum alloy wire rod |
US9991024B2 (en) | 2013-03-29 | 2018-06-05 | Furukawa Electric Co., Ltd. | Aluminum alloy wire rod, aluminum alloy stranded wire, coated wire, wire harness and manufacturing method of aluminum alloy wire rod |
KR101915585B1 (ko) | 2017-04-28 | 2018-11-07 | (주)메탈링크 | 고장력 및 고내열성의 알루미늄합금, 이에 의해 제조된 알루미늄합금선 및 가공송전선 |
Families Citing this family (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2016225159A (ja) * | 2015-06-01 | 2016-12-28 | 矢崎総業株式会社 | アルミニウム電線及びワイヤーハーネス |
JP2017218645A (ja) * | 2016-06-09 | 2017-12-14 | 矢崎総業株式会社 | アルミニウム合金電線及びそれを用いた自動車用ワイヤーハーネス |
JP6684176B2 (ja) * | 2016-07-13 | 2020-04-22 | 古河電気工業株式会社 | アルミニウム合金線材、アルミニウム合金撚線、被覆電線およびワイヤーハーネス |
US11532407B2 (en) | 2016-07-21 | 2022-12-20 | Universite Du Quebec A Chicoutimi | Aluminum conductor alloys having improved creeping resistance |
AR106253A1 (es) * | 2016-10-04 | 2017-12-27 | Di Ciommo José Antonio | Cable aéreo para transporte de energía eléctrica en baja y media tensión y de señales digitales, de conductores concéntricos de aleación de aluminio conteniendo dentro un cable de fibra óptica y proceso de tratamiento de alambre trefilado |
CN113409982B (zh) * | 2016-10-31 | 2023-02-17 | 住友电气工业株式会社 | 铝合金线、铝合金绞合线、包覆电线以及带端子电线 |
Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5188457A (en) * | 1975-02-01 | 1976-08-03 | Aruminiumusenno seizohoho | |
JPS5380312A (en) * | 1976-12-27 | 1978-07-15 | Fuji Electric Co Ltd | Preparation of conductor of aluminium alloy for winding |
JPS5411242B1 (ja) | 1970-11-16 | 1979-05-14 | ||
JP2006019163A (ja) | 2004-07-02 | 2006-01-19 | Furukawa Electric Co Ltd:The | アルミ導電線 |
JP2006253109A (ja) | 2005-02-08 | 2006-09-21 | Furukawa Electric Co Ltd:The | アルミニウム導電線 |
JP2008112620A (ja) | 2006-10-30 | 2008-05-15 | Auto Network Gijutsu Kenkyusho:Kk | 電線導体およびその製造方法 |
JP2010163675A (ja) * | 2009-01-19 | 2010-07-29 | Furukawa Electric Co Ltd:The | アルミニウム合金線材 |
JP4609866B2 (ja) * | 2009-01-19 | 2011-01-12 | 古河電気工業株式会社 | アルミニウム合金線材 |
Family Cites Families (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3600500A (en) * | 1969-06-02 | 1971-08-17 | Southwire Co | Twin conductor with filler |
WO2010082670A1 (ja) * | 2009-01-19 | 2010-07-22 | 古河電気工業株式会社 | アルミニウム合金線材 |
JP2010163676A (ja) * | 2009-01-19 | 2010-07-29 | Furukawa Electric Co Ltd:The | アルミニウム合金線材 |
-
2012
- 2012-03-29 JP JP2012527143A patent/JP5184719B2/ja active Active
- 2012-03-29 EP EP12763805.4A patent/EP2692880B1/en active Active
- 2012-03-29 WO PCT/JP2012/058335 patent/WO2012133634A1/ja active Application Filing
- 2012-03-29 CN CN201280016455.1A patent/CN103492597B/zh active Active
-
2013
- 2013-09-26 US US14/037,869 patent/US20140020796A1/en not_active Abandoned
Patent Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5411242B1 (ja) | 1970-11-16 | 1979-05-14 | ||
JPS5188457A (en) * | 1975-02-01 | 1976-08-03 | Aruminiumusenno seizohoho | |
JPS5380312A (en) * | 1976-12-27 | 1978-07-15 | Fuji Electric Co Ltd | Preparation of conductor of aluminium alloy for winding |
JP2006019163A (ja) | 2004-07-02 | 2006-01-19 | Furukawa Electric Co Ltd:The | アルミ導電線 |
JP2006253109A (ja) | 2005-02-08 | 2006-09-21 | Furukawa Electric Co Ltd:The | アルミニウム導電線 |
JP2008112620A (ja) | 2006-10-30 | 2008-05-15 | Auto Network Gijutsu Kenkyusho:Kk | 電線導体およびその製造方法 |
JP2010163675A (ja) * | 2009-01-19 | 2010-07-29 | Furukawa Electric Co Ltd:The | アルミニウム合金線材 |
JP4609866B2 (ja) * | 2009-01-19 | 2011-01-12 | 古河電気工業株式会社 | アルミニウム合金線材 |
Non-Patent Citations (1)
Title |
---|
See also references of EP2692880A4 * |
Cited By (15)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP3260563A1 (en) * | 2013-03-29 | 2017-12-27 | Furukawa Electric Co. Ltd. | Aluminum alloy conductor, aluminum alloy stranded wire, coated wire, wire harness, and manufacturing method of aluminum alloy conductor |
CN107254611A (zh) * | 2013-03-29 | 2017-10-17 | 古河电器工业株式会社 | 铝合金导体、铝合金绞线、被覆电线、线束以及铝合金导体的制造方法 |
EP2896708A1 (en) * | 2013-03-29 | 2015-07-22 | Furukawa Electric Co., Ltd. | Aluminum alloy conductor, alum1inum alloy stranded wire, sheathed wire, wire harness, and method for manufacturing aluminum alloy conductor |
CN104781431B (zh) * | 2013-03-29 | 2018-08-24 | 古河电器工业株式会社 | 铝合金导体、铝合金绞线、被覆电线、线束以及铝合金导体的制造方法 |
EP2896708A4 (en) * | 2013-03-29 | 2016-06-01 | Furukawa Electric Co Ltd | ALUMINUM ALLOY DRIVER, ALUMINUM ALLOY MULTIBORNE WIRE, THREADED WIRE, WIRE HARNESS, AND ALUMINUM ALLOY DRIVER MANUFACTURING METHOD |
EP2896706A4 (en) * | 2013-03-29 | 2016-08-03 | Furukawa Electric Co Ltd | ALUMINUM ALLOY DRIVER, ALUMINUM ALLOY TWISTED WIRE, COATED ELECTRICAL WIRE, WIRE HARNESS, AND PRODUCTION METHOD FOR ALUMINUM ALLOY DRIVERS |
CN104781431A (zh) * | 2013-03-29 | 2015-07-15 | 古河电器工业株式会社 | 铝合金导体、铝合金绞线、被覆电线、线束以及铝合金导体的制造方法 |
US9991024B2 (en) | 2013-03-29 | 2018-06-05 | Furukawa Electric Co., Ltd. | Aluminum alloy wire rod, aluminum alloy stranded wire, coated wire, wire harness and manufacturing method of aluminum alloy wire rod |
US9650706B2 (en) | 2013-03-29 | 2017-05-16 | Furukawa Electric Co., Ltd. | Aluminum alloy wire rod, aluminum alloy stranded wire, coated wire, wire harness and manufacturing method of aluminum alloy wire rod |
EP3266891A1 (en) * | 2013-03-29 | 2018-01-10 | Furukawa Electric Co. Ltd. | Aluminum alloy conductor, aluminum alloy stranded wire, coated wire, wire harness and manufacturing method of aluminum alloy conductor |
CN104217784A (zh) * | 2013-05-28 | 2014-12-17 | 尼克桑斯公司 | 电导线及其制造方法 |
US9870841B2 (en) | 2014-09-22 | 2018-01-16 | Furukawa Electric Co., Ltd. | Aluminum alloy wire rod, aluminum alloy stranded wire, coated wire, wire harness and manufacturing method of aluminum alloy wire rod |
JPWO2016047617A1 (ja) * | 2014-09-22 | 2017-07-06 | 古河電気工業株式会社 | アルミニウム合金線材、アルミニウム合金撚線、被覆電線、ワイヤーハーネスおよびアルミニウム合金線材の製造方法 |
WO2016047617A1 (ja) * | 2014-09-22 | 2016-03-31 | 古河電気工業株式会社 | アルミニウム合金線材、アルミニウム合金撚線、被覆電線、ワイヤーハーネスおよびアルミニウム合金線材の製造方法 |
KR101915585B1 (ko) | 2017-04-28 | 2018-11-07 | (주)메탈링크 | 고장력 및 고내열성의 알루미늄합금, 이에 의해 제조된 알루미늄합금선 및 가공송전선 |
Also Published As
Publication number | Publication date |
---|---|
EP2692880B1 (en) | 2016-08-03 |
JPWO2012133634A1 (ja) | 2014-07-28 |
JP5184719B2 (ja) | 2013-04-17 |
CN103492597B (zh) | 2016-01-13 |
CN103492597A (zh) | 2014-01-01 |
US20140020796A1 (en) | 2014-01-23 |
EP2692880A4 (en) | 2015-04-01 |
EP2692880A1 (en) | 2014-02-05 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP5184719B2 (ja) | アルミニウム合金導体 | |
US9580784B2 (en) | Aluminum alloy wire and method of producing the same | |
JP4986251B2 (ja) | アルミニウム合金導体 | |
JP5193375B2 (ja) | アルミニウム合金導体の製造方法 | |
JP5607855B1 (ja) | アルミニウム合金線材、アルミニウム合金撚線、被覆電線、ワイヤーハーネスおよびアルミニウム合金線材の製造方法 | |
JP5193374B2 (ja) | アルミニウム合金導体及びその製造方法 | |
JP4986252B2 (ja) | アルミニウム合金導体 | |
WO2014155819A1 (ja) | アルミニウム合金導体、アルミニウム合金撚線、被覆電線、ワイヤーハーネスおよびアルミニウム合金導体の製造方法 | |
EP2381001A1 (en) | Aluminum alloy wire | |
JP2013044038A (ja) | アルミニウム合金導体 | |
JP6440476B2 (ja) | アルミニウム合金線材、アルミニウム合金撚線、被覆電線およびワイヤーハーネス、ならびにアルミニウム合金線材の製造方法 | |
JP5939530B2 (ja) | アルミニウム合金導体 | |
US9991024B2 (en) | Aluminum alloy wire rod, aluminum alloy stranded wire, coated wire, wire harness and manufacturing method of aluminum alloy wire rod | |
JP5846360B2 (ja) | アルミニウム合金導体 | |
JP4986253B2 (ja) | アルミニウム合金導体 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
ENP | Entry into the national phase |
Ref document number: 2012527143 Country of ref document: JP Kind code of ref document: A |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 12763805 Country of ref document: EP Kind code of ref document: A1 |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
REEP | Request for entry into the european phase |
Ref document number: 2012763805 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2012763805 Country of ref document: EP |