WO2011105586A1 - Aluminum alloy conductor - Google Patents
Aluminum alloy conductor Download PDFInfo
- 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
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- aluminum alloy
- conductor
- intermetallic compound
- alloy conductor
- wire
- Prior art date
Links
- 239000004020 conductor Substances 0.000 title claims abstract description 80
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 52
- 229910000765 intermetallic Inorganic materials 0.000 claims abstract description 72
- 229940126062 Compound A Drugs 0.000 claims abstract description 18
- NLDMNSXOCDLTTB-UHFFFAOYSA-N Heterophylliin A Natural products O1C2COC(=O)C3=CC(O)=C(O)C(O)=C3C3=C(O)C(O)=C(O)C=C3C(=O)OC2C(OC(=O)C=2C=C(O)C(O)=C(O)C=2)C(O)C1OC(=O)C1=CC(O)=C(O)C(O)=C1 NLDMNSXOCDLTTB-UHFFFAOYSA-N 0.000 claims abstract description 18
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 238000010438 heat treatment Methods 0.000 claims description 25
- 239000002245 particle Substances 0.000 claims description 24
- 238000001816 cooling Methods 0.000 claims description 19
- 238000005491 wire drawing Methods 0.000 claims description 19
- 238000000034 method Methods 0.000 claims description 12
- 239000013078 crystal Substances 0.000 claims description 11
- 238000004519 manufacturing process Methods 0.000 claims description 5
- 230000008569 process Effects 0.000 claims description 4
- 229910052782 aluminium Inorganic materials 0.000 abstract description 22
- 150000001875 compounds Chemical class 0.000 abstract 2
- 238000000137 annealing Methods 0.000 description 47
- 238000005452 bending Methods 0.000 description 31
- 230000000052 comparative effect Effects 0.000 description 21
- 238000005266 casting Methods 0.000 description 18
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 17
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 17
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 11
- 229910052802 copper Inorganic materials 0.000 description 11
- 239000010949 copper Substances 0.000 description 11
- 239000000463 material Substances 0.000 description 8
- 229910018084 Al-Fe Inorganic materials 0.000 description 6
- 229910018192 Al—Fe Inorganic materials 0.000 description 6
- 239000000654 additive Substances 0.000 description 6
- 230000000996 additive effect Effects 0.000 description 6
- 229910052742 iron Inorganic materials 0.000 description 6
- 239000000523 sample Substances 0.000 description 6
- 229910018191 Al—Fe—Si Inorganic materials 0.000 description 5
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 230000007423 decrease Effects 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 238000005498 polishing Methods 0.000 description 5
- 238000012545 processing Methods 0.000 description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 5
- 229910018580 Al—Zr Inorganic materials 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 239000002244 precipitate Substances 0.000 description 4
- 238000005096 rolling process Methods 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 229910000881 Cu alloy Inorganic materials 0.000 description 3
- 238000009749 continuous casting Methods 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 229910052726 zirconium Inorganic materials 0.000 description 3
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 2
- 230000005540 biological transmission Effects 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 238000009434 installation Methods 0.000 description 2
- VLTRZXGMWDSKGL-UHFFFAOYSA-N perchloric acid Chemical compound OCl(=O)(=O)=O VLTRZXGMWDSKGL-UHFFFAOYSA-N 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 239000010409 thin film Substances 0.000 description 2
- CYJRNFFLTBEQSQ-UHFFFAOYSA-N 8-(3-methyl-1-benzothiophen-5-yl)-N-(4-methylsulfonylpyridin-3-yl)quinoxalin-6-amine Chemical compound CS(=O)(=O)C1=C(C=NC=C1)NC=1C=C2N=CC=NC2=C(C=1)C=1C=CC2=C(C(=CS2)C)C=1 CYJRNFFLTBEQSQ-UHFFFAOYSA-N 0.000 description 1
- 229910001369 Brass Inorganic materials 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910052787 antimony Inorganic materials 0.000 description 1
- WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000010951 brass Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 229940125810 compound 20 Drugs 0.000 description 1
- 230000008094 contradictory effect Effects 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000009429 electrical wiring Methods 0.000 description 1
- 230000005611 electricity Effects 0.000 description 1
- 238000010894 electron beam technology Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 238000009661 fatigue test Methods 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 230000005855 radiation Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 239000011347 resin Substances 0.000 description 1
- 229920005989 resin Polymers 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
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
- 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.
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)
- Insulated Conductors (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.
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.
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.
(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.
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.
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%.
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.
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.
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.
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.
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.
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.
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.
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.
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.
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.
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.
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.
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.
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)
- 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 - 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: - 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.
- 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.
- 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.
- 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.
- 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.
- 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.
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2011528135A JP4986253B2 (en) | 2010-02-26 | 2011-02-25 | Aluminum alloy conductor |
EP11747542.6A EP2540850B1 (en) | 2010-02-26 | 2011-02-25 | Aluminum alloy conductor |
CN201180010674.4A CN102803531B (en) | 2010-02-26 | 2011-02-25 | Aluminium alloy conductor |
US13/594,480 US20120321507A1 (en) | 2010-02-26 | 2012-08-24 | Aluminum alloy conductor |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2010043489 | 2010-02-26 | ||
JP2010-043489 | 2010-02-26 |
Related Child Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US13/594,480 Continuation US20120321507A1 (en) | 2010-02-26 | 2012-08-24 | Aluminum alloy conductor |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2011105586A1 true WO2011105586A1 (en) | 2011-09-01 |
Family
ID=44506983
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2011/054399 WO2011105586A1 (en) | 2010-02-26 | 2011-02-25 | Aluminum alloy conductor |
Country Status (5)
Country | Link |
---|---|
US (1) | US20120321507A1 (en) |
EP (1) | EP2540850B1 (en) |
JP (1) | JP4986253B2 (en) |
CN (1) | CN102803531B (en) |
WO (1) | WO2011105586A1 (en) |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2012008588A1 (en) * | 2010-07-15 | 2012-01-19 | 古河電気工業株式会社 | Aluminum alloy conductor |
EP2754725A4 (en) * | 2011-09-05 | 2015-06-17 | Dyden Corp | Aluminum-based electroconductive material, and electric wire and cable obtained using same |
JP2016180186A (en) * | 2012-03-29 | 2016-10-13 | 大電株式会社 | Production method of microcrystal metal conductor, and microcrystal metal conductor |
JP2017525845A (en) * | 2014-07-03 | 2017-09-07 | エルエス ケーブル アンド システム リミテッド. | Aluminum alloy conductor wire and method for manufacturing the same |
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 |
Citations (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5132409A (en) * | 1974-09-13 | 1976-03-19 | Hitachi Cable | DODENYOARUMINIUMUGOKIN OYOBI DODENYOARUMINIUMUGOKINSENNARABINISONOSEIZOHOHO |
JPS54132417A (en) * | 1968-05-21 | 1979-10-15 | Southwire Co | Production of aluminum alloy wire |
JPS5545626B2 (en) | 1976-12-27 | 1980-11-19 | ||
JPS5827948A (en) * | 1981-08-13 | 1983-02-18 | Tokyo Electric Power Co Inc:The | Electrically conductive heat-resistant aluminum alloy wire |
JP2004311102A (en) * | 2003-04-03 | 2004-11-04 | Hitachi Cable Ltd | Aluminum alloy wiring material and its manufacturing method |
JP2006004752A (en) * | 2004-06-17 | 2006-01-05 | Furukawa Electric Co Ltd:The | Aluminum conductive wire |
JP2006019163A (en) | 2004-07-02 | 2006-01-19 | Furukawa Electric Co Ltd:The | Aluminum conductive wire |
JP2006253109A (en) | 2005-02-08 | 2006-09-21 | Furukawa Electric Co Ltd:The | Aluminum conductive wire |
JP2008112620A (en) | 2006-10-30 | 2008-05-15 | Auto Network Gijutsu Kenkyusho:Kk | Electric wire conductor and its manufacturing method |
WO2010018646A1 (en) * | 2008-08-11 | 2010-02-18 | 住友電気工業株式会社 | Aluminum alloy wire |
JP2010043489A (en) | 2008-08-18 | 2010-02-25 | Toppan Cosmo Inc | Molding for surface material |
Family Cites Families (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3958987A (en) * | 1975-03-17 | 1976-05-25 | Southwire Company | Aluminum iron cobalt silicon alloy and method of preparation thereof |
GB1469334A (en) * | 1974-04-16 | 1977-04-06 | Southwire Co | Aluminiuj alloy used for electrical conductors and process for preparing same |
FR2286886A1 (en) * | 1974-10-04 | 1976-04-30 | Pechiney Aluminium | ELECTRICAL CONDUCTORS IN ALUMINUM ALLOYS AND METHODS OF OBTAINING |
US4028141A (en) * | 1975-03-12 | 1977-06-07 | Southwire Company | Aluminum iron silicon alloy |
FR2311391A1 (en) * | 1975-05-14 | 1976-12-10 | Pechiney Aluminium | ELECTRICAL CONDUCTORS IN AL FE ALLOYS OBTAINED BY SHELL SPINNING |
JPS5810465B2 (en) * | 1978-12-06 | 1983-02-25 | 関西電力株式会社 | Manufacturing method of highly heat-resistant aluminum alloy for conductive use |
BR8103057A (en) * | 1981-05-18 | 1982-12-21 | Pirelli Sa | ALUMINUM ALLOY FOR ELECTRICAL CONDUCTORS AND PROCESS FOR THEIR OBTAINING |
-
2011
- 2011-02-25 JP JP2011528135A patent/JP4986253B2/en active Active
- 2011-02-25 EP EP11747542.6A patent/EP2540850B1/en active Active
- 2011-02-25 CN CN201180010674.4A patent/CN102803531B/en active Active
- 2011-02-25 WO PCT/JP2011/054399 patent/WO2011105586A1/en active Application Filing
-
2012
- 2012-08-24 US US13/594,480 patent/US20120321507A1/en not_active Abandoned
Patent Citations (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS54132417A (en) * | 1968-05-21 | 1979-10-15 | Southwire Co | Production of aluminum alloy wire |
JPS5132409A (en) * | 1974-09-13 | 1976-03-19 | Hitachi Cable | DODENYOARUMINIUMUGOKIN OYOBI DODENYOARUMINIUMUGOKINSENNARABINISONOSEIZOHOHO |
JPS5545626B2 (en) | 1976-12-27 | 1980-11-19 | ||
JPS5827948A (en) * | 1981-08-13 | 1983-02-18 | Tokyo Electric Power Co Inc:The | Electrically conductive heat-resistant aluminum alloy wire |
JP2004311102A (en) * | 2003-04-03 | 2004-11-04 | Hitachi Cable Ltd | Aluminum alloy wiring material and its manufacturing method |
JP2006004752A (en) * | 2004-06-17 | 2006-01-05 | Furukawa Electric Co Ltd:The | Aluminum conductive wire |
JP2006019163A (en) | 2004-07-02 | 2006-01-19 | Furukawa Electric Co Ltd:The | Aluminum conductive wire |
JP2006253109A (en) | 2005-02-08 | 2006-09-21 | Furukawa Electric Co Ltd:The | Aluminum conductive wire |
JP2008112620A (en) | 2006-10-30 | 2008-05-15 | Auto Network Gijutsu Kenkyusho:Kk | Electric wire conductor and its manufacturing method |
WO2010018646A1 (en) * | 2008-08-11 | 2010-02-18 | 住友電気工業株式会社 | Aluminum alloy wire |
JP2010043489A (en) | 2008-08-18 | 2010-02-25 | Toppan Cosmo Inc | Molding for surface material |
Non-Patent Citations (1)
Title |
---|
See also references of EP2540850A4 |
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2012008588A1 (en) * | 2010-07-15 | 2012-01-19 | 古河電気工業株式会社 | Aluminum alloy conductor |
EP2754725A4 (en) * | 2011-09-05 | 2015-06-17 | Dyden Corp | Aluminum-based electroconductive material, and electric wire and cable obtained using same |
US9779849B2 (en) | 2011-09-05 | 2017-10-03 | Dyden Corporation | Aluminum-based conductive material and electric wire and cable using the same |
JP2016180186A (en) * | 2012-03-29 | 2016-10-13 | 大電株式会社 | Production method of microcrystal metal conductor, and microcrystal metal conductor |
JP2017525845A (en) * | 2014-07-03 | 2017-09-07 | エルエス ケーブル アンド システム リミテッド. | Aluminum alloy conductor wire and method for manufacturing the same |
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 |
Also Published As
Publication number | Publication date |
---|---|
JPWO2011105586A1 (en) | 2013-06-20 |
CN102803531B (en) | 2015-11-25 |
EP2540850A1 (en) | 2013-01-02 |
JP4986253B2 (en) | 2012-07-25 |
EP2540850B1 (en) | 2017-11-15 |
US20120321507A1 (en) | 2012-12-20 |
CN102803531A (en) | 2012-11-28 |
EP2540850A4 (en) | 2013-11-06 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP4986251B2 (en) | Aluminum alloy conductor | |
JP4986252B2 (en) | Aluminum alloy conductor | |
JP5367926B1 (en) | Aluminum alloy wire and manufacturing method thereof | |
JP5193375B2 (en) | Method for producing aluminum alloy conductor | |
US8951370B2 (en) | Aluminum alloy wire material | |
JP5193374B2 (en) | Aluminum alloy conductor and method for producing the same | |
KR101898321B1 (en) | Aluminum alloy conductor, aluminum alloy twisted wire, coated electric wire, wire harness, and production method for aluminum alloy conductors | |
JP5184719B2 (en) | Aluminum alloy conductor | |
JP2013044038A (en) | Aluminum alloy conductor | |
JP6440476B2 (en) | Aluminum alloy wire, aluminum alloy twisted wire, covered electric wire and wire harness, and method for producing aluminum alloy wire | |
JP2010163675A (en) | Aluminum alloy wire rod | |
JP5939530B2 (en) | Aluminum alloy conductor | |
JP4986253B2 (en) | Aluminum alloy conductor | |
JP5846360B2 (en) | Aluminum alloy conductor |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
WWE | Wipo information: entry into national phase |
Ref document number: 201180010674.4 Country of ref document: CN |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2011528135 Country of ref document: JP |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 11747542 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: 2011747542 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2011747542 Country of ref document: EP |