WO2014155817A1 - 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 - Google Patents
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 Download PDFInfo
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- WO2014155817A1 WO2014155817A1 PCT/JP2013/080955 JP2013080955W WO2014155817A1 WO 2014155817 A1 WO2014155817 A1 WO 2014155817A1 JP 2013080955 W JP2013080955 W JP 2013080955W WO 2014155817 A1 WO2014155817 A1 WO 2014155817A1
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- aluminum alloy
- wire
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- alloy conductor
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 112
- 239000004020 conductor Substances 0.000 title claims abstract description 72
- 238000004519 manufacturing process Methods 0.000 title claims description 18
- 238000005452 bending Methods 0.000 claims abstract description 51
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 45
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 44
- 150000001875 compounds Chemical class 0.000 claims abstract description 43
- 239000013078 crystal Substances 0.000 claims abstract description 31
- 239000000203 mixture Substances 0.000 claims abstract description 16
- 239000012535 impurity Substances 0.000 claims abstract description 11
- 239000002245 particle Substances 0.000 claims abstract description 9
- 238000010438 heat treatment Methods 0.000 claims description 175
- 238000001816 cooling Methods 0.000 claims description 59
- 229910019018 Mg 2 Si Inorganic materials 0.000 claims description 30
- 230000032683 aging Effects 0.000 claims description 27
- 229910052802 copper Inorganic materials 0.000 claims description 24
- 238000005491 wire drawing Methods 0.000 claims description 24
- 229910052782 aluminium Inorganic materials 0.000 claims description 23
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 22
- 239000006185 dispersion Substances 0.000 claims description 17
- 238000005266 casting Methods 0.000 claims description 14
- 229910052709 silver Inorganic materials 0.000 claims description 13
- 229910052759 nickel Inorganic materials 0.000 claims description 12
- 229910052706 scandium Inorganic materials 0.000 claims description 12
- 229910052719 titanium Inorganic materials 0.000 claims description 11
- 229910052720 vanadium Inorganic materials 0.000 claims description 11
- 229910052796 boron Inorganic materials 0.000 claims description 10
- 229910052804 chromium Inorganic materials 0.000 claims description 10
- 229910052735 hafnium Inorganic materials 0.000 claims description 10
- 229910052742 iron Inorganic materials 0.000 claims description 10
- 229910052726 zirconium Inorganic materials 0.000 claims description 10
- 238000010521 absorption reaction Methods 0.000 claims description 8
- 238000002844 melting Methods 0.000 claims description 7
- 230000008018 melting Effects 0.000 claims description 7
- 239000000126 substance Substances 0.000 claims description 7
- 229910045601 alloy Inorganic materials 0.000 claims description 4
- 239000000956 alloy Substances 0.000 claims description 4
- 239000011247 coating layer Substances 0.000 claims description 4
- 238000009661 fatigue test Methods 0.000 claims description 4
- 229910052737 gold Inorganic materials 0.000 claims description 3
- 239000010410 layer Substances 0.000 claims description 2
- 229910052748 manganese Inorganic materials 0.000 claims description 2
- 230000035939 shock Effects 0.000 abstract description 4
- 229910019752 Mg2Si Inorganic materials 0.000 abstract 1
- 239000011777 magnesium Substances 0.000 description 63
- 239000010949 copper Substances 0.000 description 25
- 238000000034 method Methods 0.000 description 24
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 22
- 230000000694 effects Effects 0.000 description 19
- 239000002244 precipitate Substances 0.000 description 14
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 11
- 230000000052 comparative effect Effects 0.000 description 11
- 230000007423 decrease Effects 0.000 description 11
- 230000008569 process Effects 0.000 description 11
- 239000000243 solution Substances 0.000 description 11
- 239000000523 sample Substances 0.000 description 10
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- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 9
- 238000000137 annealing Methods 0.000 description 8
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- 239000000654 additive Substances 0.000 description 5
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- 229910000765 intermetallic Inorganic materials 0.000 description 5
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- 238000007373 indentation Methods 0.000 description 4
- 230000007246 mechanism Effects 0.000 description 4
- 238000005096 rolling process Methods 0.000 description 4
- 229910018084 Al-Fe Inorganic materials 0.000 description 3
- 229910018192 Al—Fe Inorganic materials 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 3
- 229910000881 Cu alloy Inorganic materials 0.000 description 3
- 229910019064 Mg-Si Inorganic materials 0.000 description 3
- 229910019406 Mg—Si Inorganic materials 0.000 description 3
- 230000009471 action Effects 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000009749 continuous casting Methods 0.000 description 3
- 229910001873 dinitrogen Inorganic materials 0.000 description 3
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- 229910052751 metal Inorganic materials 0.000 description 3
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- 239000010409 thin film Substances 0.000 description 2
- 229910018191 Al—Fe—Si Inorganic materials 0.000 description 1
- 229910018464 Al—Mg—Si Inorganic materials 0.000 description 1
- 229910001369 Brass Inorganic materials 0.000 description 1
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 1
- 229910007981 Si-Mg Inorganic materials 0.000 description 1
- 229910008316 Si—Mg Inorganic materials 0.000 description 1
- 229910052797 bismuth Inorganic materials 0.000 description 1
- 239000010951 brass Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
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- 238000007796 conventional method Methods 0.000 description 1
- 238000002788 crimping Methods 0.000 description 1
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- 238000011156 evaluation Methods 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 229910052733 gallium Inorganic materials 0.000 description 1
- 230000017525 heat dissipation Effects 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000009434 installation Methods 0.000 description 1
- 238000010884 ion-beam technique Methods 0.000 description 1
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- 230000000630 rising effect Effects 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
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- 229910052725 zinc Inorganic materials 0.000 description 1
Classifications
-
- 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
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium 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
- C22C21/14—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
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/057—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with copper as the next major constituent
-
- 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
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B1/00—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors
- H01B1/02—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors mainly consisting of metals or alloys
- H01B1/023—Alloys based on aluminium
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B5/00—Non-insulated conductors or conductive bodies characterised by their form
- H01B5/02—Single bars, rods, wires, or strips
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B7/00—Insulated conductors or cables characterised by their form
- H01B7/0045—Cable-harnesses
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
Definitions
- the present invention relates to an aluminum alloy conductor, an aluminum alloy twisted wire, a covered electric wire, a wire harness, and a method for producing an aluminum alloy conductor used as a conductor of an electric wiring body, and particularly as an ultrafine wire having a strand diameter of 0.5 mm or less. Even when used, the present invention relates to an aluminum alloy conductor having improved impact resistance and flexural fatigue resistance while ensuring the same level of strength, elongation and conductivity as conventional products.
- an electric wiring body of a moving body such as an automobile, a train, an aircraft, or an electric wiring body of an industrial robot
- a terminal made of copper or a copper alloy for example, brass
- a so-called wire harness member equipped with a connector has been used.
- the performance and functionality of automobiles have been rapidly advanced, and as a result, the number of various electric devices and control devices mounted on the vehicle has increased, and these devices are used in these devices.
- the means for achieving such weight reduction of the moving body for example, it is considered to replace the conductor of the electric wiring body with a lighter aluminum or aluminum alloy instead of the conventionally used copper or copper alloy. It is being advanced.
- the specific gravity of aluminum is about 1/3 of the specific gravity of copper
- the electrical conductivity of aluminum is about 2/3 of the electrical conductivity of copper (pure aluminum is about 66% IACS when pure copper is used as a standard of 100% IACS).
- the cross-sectional area of the aluminum conductor wire needs to be about 1.5 times the cross-sectional area of the copper conductor wire.
- 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.
- pure aluminum wires represented by aluminum alloy wires for power transmission lines are generally inferior in tensile durability, impact resistance, bending characteristics, and the like. For this reason, for example, a load that is unexpectedly applied by an operator or industrial equipment during installation to the vehicle body, a tension at a crimping portion at a connection portion between an electric wire and a terminal, or a load at a bending portion such as a door portion. It cannot withstand stress.
- materials alloyed by adding various additive elements can increase the tensile strength, it causes a decrease in conductivity due to the solid solution phenomenon of the additive elements in aluminum, and excessive metal in the aluminum.
- the intermetallic compound By forming the intermetallic compound, disconnection due to the intermetallic compound may occur during wire drawing. Therefore, by limiting or selecting the additive element, it is essential that it has sufficient elongation characteristics, so that it is not necessary to break, and further, impact resistance and bending characteristics are improved while ensuring the conventional level of conductivity and tensile strength. It was necessary to let them.
- a high-strength aluminum alloy wire for example, an aluminum alloy wire containing Mg and Si is known, and a typical example of the aluminum alloy wire is a 6000 series aluminum alloy (Al—Mg—Si based alloy) wire.
- the 6000 series aluminum alloy wire can be strengthened by subjecting it to a solution treatment and an aging treatment.
- high strength can be achieved by solution treatment and aging treatment, but elongation tends to be insufficient. .
- Patent Document 1 A conventional 6000 series aluminum alloy wire used for an electric wiring body of a moving body is described in Patent Document 1, for example.
- the aluminum alloy wire described in Patent Document 1 is an ultrathin wire, and realizes an aluminum alloy wire that has high strength and high electrical conductivity and is excellent in elongation.
- Patent Document 1 describes that it has excellent bending properties because it has good elongation.
- an aluminum alloy wire is used as a wire harness attached to a door portion, and the door is opened and closed. There is no disclosure or suggestion about impact resistance or bending fatigue resistance in a use environment in which repeated bending stress is likely to cause fatigue failure.
- the object of the present invention is based on the premise that an aluminum alloy containing Mg and Si is used, and by suppressing grain boundary segregation caused by the Mg component and the Si component, in particular, the strand diameter is 0.5 mm or less. Even when used as an extra fine wire, it has improved impact resistance and bending fatigue resistance while ensuring the same level of strength, elongation, and conductivity as the conventional product (aluminum alloy wire described in Patent Document 1).
- An object of the present invention is to provide an aluminum alloy conductor, an aluminum alloy twisted wire, a covered electric wire and a wire harness used as a conductor of an electric wiring body, and to provide a method for producing an aluminum alloy conductor.
- the present inventors As a result of observing the microstructure of a conventional aluminum alloy conductor containing Mg and Si, the present inventors have found that a concentrated portion of Si element and a concentrated portion of Mg element are formed at the grain boundary. did. For this reason, the present inventors, as a result of the presence of Si element enriched portion and Mg element enriched portion in the crystal grain boundary, the interface bond between these enriched portions and the aluminum matrix is weakened, Intensive study was conducted under the assumption that tensile strength, elongation, impact resistance and bending fatigue resistance deteriorate. Then, the present inventors produced various aluminum alloy conductors in which the concentration of the concentrated portion of Si element and the concentrated portion of Mg element present in the grain boundary was changed by controlling the component composition and the manufacturing process.
- the gist configuration of the present invention is as follows. (1) Mg: 0.1 to 1.0 mass%, Si: 0.1 to 1.0 mass%, Fe: 0.01 to 1.40 mass%, Ti: 0.000 to 0.100 mass% , B: 0.000 to 0.030 mass%, Cu: 0.00 to 1.00 mass%, Ag: 0.00 to 0.50 mass%, Au: 0.00 to 0.50 mass%, Mn : 0.00 to 1.00% by mass, Cr: 0.00 to 1.00% by mass, Zr: 0.00 to 0.50% by mass, Hf: 0.00 to 0.50% by mass, V: 0 0.00 to 0.50 mass%, Sc: 0.00 to 0.50 mass%, Co: 0.00 to 0.50 mass%, Ni: 0.00 to 0.50 mass%, the balance: Al and inevitable
- the dispersion density of the Mg 2 Si compound having an impurity composition and a particle diameter of 0.5 to 5.0 ⁇ m is 3.0 ⁇ 10 ⁇ 3 particles / ⁇ m 2 or less, and the same as the crystal grains of
- the chemical composition contains one or two selected from the group consisting of Ti: 0.001 to 0.100 mass% and B: 0.001 to 0.030 mass%.
- the chemical composition is Cu: 0.01 to 1.00% by mass, Ag: 0.01 to 0.50% by mass, Au: 0.01 to 0.50% by mass, Mn: 0.01 to 1.00% by mass, Cr: 0.01-1.00% by mass, Zr: 0.01-0.50% by mass, Hf: 0.01-0.50% by mass, V: 0.01-0.
- the total content of Fe, Ti, B, Cu, Ag, Au, Mn, Cr, Zr, Hf, V, Sc, Co, and Ni is 0.01 to 2.00% by mass (1)
- a wire harness comprising the covered electric wire according to (9) and a terminal attached to an end of the covered electric wire from which the covering layer is removed.
- a hot wire is formed to form a rough drawn wire, and then the first wire drawing, the first heat treatment, the second wire drawing, the second heat treatment, and the aging heat treatment are sequentially performed.
- the first heat treatment is performed by heating to a predetermined temperature within a range of 480 to 620 ° C. and then cooling at an average cooling rate of 10 ° C./s or more to a temperature of at least 150 ° C.
- cooling is performed at an average cooling rate of 9 ° C./s or higher to a temperature of at least 150 ° C.
- the method for producing an aluminum alloy conductor according to any one of (1) to (7) above.
- the aluminum alloy conductor of the present invention is based on the premise that an aluminum alloy containing Mg and Si is used, and suppresses grain boundary segregation caused by the Mg component and the Si component. Even when used as an extra fine wire, the impact resistance and bending fatigue resistance are improved while ensuring the same level of strength, elongation and conductivity as the conventional product (aluminum alloy wire described in Patent Document 1) It is possible to provide an aluminum alloy conductor, an aluminum alloy twisted wire, a covered electric wire, a wire harness used as a conductor of an electric wiring body, and to provide a method for producing an aluminum alloy conductor, which is mounted on a moving body.
- the aluminum alloy conductor of the present invention has high tensile strength, it is also possible to make the wire diameter thinner than conventional wires, and doors and trunks that are required to have high impact resistance and bending fatigue resistance, It can be suitably used for a bonnet or the like.
- the aluminum alloy conductor of the present invention has Mg: 0.10 to 1.00% by mass, Si: 0.10 to 1.00% by mass, Fe: 0.01 to 1.40% by mass, Ti: 0.000 to 0.100% by mass, B: 0.000-0.030% by mass, Cu: 0.00-1.00% by mass, Ag: 0.00-0.50% by mass, Au: 0.00-0.
- the balance has a composition of Al and inevitable impurities, the dispersion density of the Mg 2 Si compound having a particle diameter of 0.5 ⁇ 5.0 .mu.m is 3.0 ⁇ 10 -3 pieces ⁇ m 2 or less, an aluminum alloy conductor in which the concentration of Si and Mg in the crystal grain boundaries of the crystal grains of the matrix phase is characterized in that both at most 2.00 mass%.
- Chemical composition ⁇ Mg: 0.10 to 1.00% by mass> Mg (magnesium) has the effect of strengthening by dissolving in an aluminum base material, and part of it combines with Si to form precipitates to improve tensile strength, bending fatigue resistance and heat resistance. It is an element having an action.
- Mg content is less than 0.10% by mass, the above-described effects are insufficient, and when the Mg content exceeds 1.00% by mass, an Mg-concentrated portion is formed at the crystal grain boundary.
- the Mg content is 0.10 to 1.00% by mass.
- the Mg content is preferably 0.50 to 1.00% by mass when high strength is important, and 0.10 to 0.50% by mass when conductivity is important. From such a viewpoint, the total content is preferably 0.30 to 0.70% by mass.
- Si is an element that has an action of combining with Mg to form a precipitate to improve tensile strength, bending fatigue resistance, and heat resistance.
- Si content is less than 0.10% by mass, the above-described effects are insufficient, and when the Si content exceeds 1.00% by mass, there is a possibility of forming a Si-concentrated portion at the crystal grain boundary. The tensile strength, the elongation, and the bending fatigue resistance are lowered, and the electrical conductivity is lowered by increasing the amount of Si element dissolved. Therefore, the Si content is 0.10 to 1.00% by mass.
- the Si content is preferably 0.50 to 1.00% by mass when high strength is important, and 0.10 to 0.50% by mass when conductivity is important. From such a viewpoint, the total content is preferably 0.30 to 0.70% by mass.
- Fe is an element that contributes to refinement of crystal grains mainly by forming an Al—Fe-based intermetallic compound and improves tensile strength and bending fatigue resistance. Fe can only dissolve at 0.05% by mass in Al at 655 ° C. and is even less at room temperature. Therefore, the remaining Fe that cannot be dissolved in Al is Al—Fe, Al—Fe—Si, Al—Fe. -Crystallizes or precipitates as an intermetallic compound such as Si-Mg. This intermetallic compound contributes to the refinement of crystal grains and improves the tensile strength and the bending fatigue resistance.
- Fe has the effect
- the aluminum alloy conductor of the present invention contains Mg, Si and Fe as essential components, but if necessary, one or two selected from the group consisting of Ti and B, Cu, Ag, Au , Mn, Cr, Zr, Hf, V, Sc, Co, and Ni can be included.
- Ti is an element having an effect of refining the structure of the ingot at the time of melt casting. If the structure of the ingot is coarse, the ingot cracking in the casting or disconnection occurs in the wire processing step, which is not industrially desirable. If the Ti content is less than 0.001% by mass, the above-mentioned effects cannot be fully exhibited, and if the Ti content exceeds 0.100% by mass, the conductivity tends to decrease. It is. Accordingly, the Ti content is set to 0.001 to 0.100 mass%, preferably 0.005 to 0.050 mass%, more preferably 0.005 to 0.030 mass%.
- B like Ti
- a coarse ingot structure is not industrially desirable because it tends to cause ingot cracking and disconnection in the wire processing step during casting.
- the B content is 0.001 to 0.030 mass%, preferably 0.001 to 0.020 mass%, more preferably 0.001 to 0.010 mass%.
- ⁇ Cu 0.01 to 1.00% by mass>, ⁇ Ag: 0.01 to 0.50% by mass>, ⁇ Au: 0.01 to 0.50% by mass>, ⁇ Mn: 0.01 to 1 .00 mass%, ⁇ Cr: 0.01 to 1.00 mass%> and ⁇ Zr: 0.01 to 0.50 mass%>, ⁇ Hf: 0.01 to 0.50 mass%>, ⁇ V : 0.01 to 0.50 mass%, ⁇ Sc: 0.01 to 0.50 mass%>, ⁇ Co: 0.01 to 0.50 mass%> ⁇ Ni: 0.01 to 0.50 mass% %> 1 type or 2 types or more Cu, Ag, Au, Mn, Cr, Zr, Hf, V, Sc, Co and Ni are all elements that have the effect of refining crystal grains.
- Cu, Ag and Au are elements that also have the effect of increasing the grain boundary strength by precipitating at the grain boundaries. If one kind is contained in an amount of 0.01% by mass or more, the above-described effects can be obtained, and tensile strength, elongation, and bending fatigue resistance can be improved. On the other hand, if any of the contents of Cu, Ag, Au, Mn, Cr, Zr, Hf, V, Sc, Co and Ni exceeds the above upper limit values, the compound containing the element becomes coarse. In order to deteriorate wire drawing workability, disconnection is likely to occur, and the conductivity tends to decrease. Therefore, the ranges of the contents of Cu, Ag, Au, Mn, Cr, Zr, Hf, V, Sc, Co, and Ni are set to the above ranges, respectively.
- the total content of these elements is preferably 2.00% by mass or less. Since Fe is an essential element in the aluminum alloy conductor of the present invention, the total content of Fe, Ti, B, Cu, Ag, Au, Mn, Cr, Zr, Hf, V, Sc, Co and Ni is 0.01 to 2.00% by mass. The content of these elements is more preferably 0.10 to 2.00% by mass. However, when these elements are added alone, the larger the content, the more the compound containing the elements tends to become coarser, which deteriorates the wire drawing workability and easily causes disconnection. In the element, the content range is as defined above.
- the total content of Sc, Co and Ni is particularly preferably 0.10 to 0.80% by mass, and further preferably 0.20 to 0.60% by mass.
- the conductivity is slightly lowered, in order to further improve the tensile strength, elongation, impact resistance, and bending fatigue resistance, it is particularly preferably more than 0.80 to 2.00% by mass, preferably 1.00 to 2%. 0.000 mass% is more preferable.
- Al and inevitable impurities The balance other than the components described above is Al (aluminum) and inevitable impurities.
- the inevitable impurities referred to here mean impurities in a content level that can be unavoidably included in the manufacturing process. Depending on the content of the inevitable impurities, it may be a factor for reducing the electrical conductivity. Therefore, it is preferable to suppress the content of the inevitable impurities to some extent in consideration of the decrease in the electrical conductivity. Examples of components listed as inevitable impurities include Ga, Zn, Bi, Pb, and the like.
- the dispersion density of the Mg 2 Si compound having a particle size of 0.5 to 5.0 ⁇ m is 3.0 ⁇ 10 ⁇ 3 particles / ⁇ m 2 or less.
- the aluminum alloy conductor of the present invention comprises crystal grains of an aluminum matrix.
- the density of the Mg 2 Si compound having a specific size existing therein is defined.
- the Mg 2 Si compound of 0.5 to 5.0 ⁇ m is mainly used when the first heat treatment described later is heat-treated at a temperature of less than 480 ° C. for 2 minutes or more, or when the cooling rate of the first heat treatment is less than 10 ° C./s. When the second heat treatment temperature is less than 480 ° C.
- the second heat treatment is performed when the cooling rate of the second heat treatment is less than 9 ° C./s.
- the dispersion density of the Mg 2 Si compound of 0.5 to 5.0 ⁇ m is formed to exceed 3.0 ⁇ 10 ⁇ 3 / ⁇ m 2 , few acicular Mg 2 Si precipitates are formed during the aging heat treatment.
- the range of improvement in tensile strength, impact resistance, bending fatigue resistance, and conductivity is reduced.
- the smaller the dispersion density of the Mg 2 Si compound of 0.5 to 5 ⁇ m the better. That is, the closer to 0, the better.
- Mg 2 Si compounds not only Mg 2 Si compounds, but also needle-like Mg 2 Si precipitates formed during aging heat treatment are reduced even if the density of the compound containing Mg—Si as the main component is outside the above specified range. Further, since the range of improvement in tensile strength, impact resistance, flexural fatigue resistance, and conductivity is small, the density of the compound containing Mg—Si as a main component is similarly set within the above specified range.
- the Si and Mg concentrations at the crystal grain boundaries between the crystal grains of the parent phase are both 2.00% by mass or less.
- the Si and Mg concentrations at the grain boundaries of the aluminum matrix are both 2.00% by mass or less.
- a concentrated portion in which at least one of the Si and Mg concentrations is higher than 2.00% by mass is formed at the crystal grain boundary, this weakens the interface between the concentrated portion of Si and Mg and the aluminum parent phase. This is because the tensile strength, elongation, impact resistance, and bending fatigue resistance are lowered, and the wire drawing workability tends to be inferior.
- the concentrations of Si and Mg at the grain boundaries are each preferably 1.50% by mass or less, and more preferably 1.20% by mass or less.
- concentration of Si and Mg is performed using an optical microscope, an electron microscope, and an electron probe microanalyzer (EPMA).
- EPMA electron probe microanalyzer
- a linear Mg or Si concentrated portion having a length of 1 ⁇ m or more existing in the grain boundary defined in the present invention is distinguished from a granular Mg or Si concentrated portion derived from a compound, The granular thickened part is excluded from measurement.
- the length of the line analysis is arbitrarily set so as to cross the concentrated portion of the crystal grain boundary. Line analysis is performed, and the maximum concentrations of the Si element and Mg element in the linear concentrated portion are measured.
- the concentration of Mg or Si at the grain boundary is regarded as 0% by mass, and the line analysis may not be performed.
- the concentration is measured by arbitrarily selecting ten linear thickened portions by such a measuring method. When 10 places cannot be measured in one field of view, observation is similarly made in another field of view, and a total of 10 linear concentrated portions are measured.
- concentrations of Si and Mg at the crystal grain boundaries of the aluminum matrix are both 2.00% by mass or less, in the measurement across the crystal grain boundaries, the direction perpendicular to the grain boundaries is used. There is no need to cross over. Even when it crosses diagonally with respect to the grain boundary, the concentration of Si and Mg may be 2.00% by mass or less.
- Such an aluminum alloy conductor in which the Si element and Mg element concentration portions are suppressed can be realized by controlling the alloy composition and manufacturing process in combination.
- the suitable manufacturing method of the aluminum alloy conductor of this invention is demonstrated.
- the aluminum alloy conductor of the present invention includes [1] melting, [2] casting, [3] hot working (groove roll machining, etc.), [4] first wire drawing, [5] first heat treatment (solution heat treatment). ), [6] Second wire drawing, [7] Second heat treatment, and [8] Aging heat treatment are sequentially performed. Note that a step of forming a stranded wire or a step of coating a wire with a resin may be provided before or after the second heat treatment or after the aging heat treatment. The steps [1] to [8] will be described below.
- the degree of work ⁇ is preferably in the range of 1-6.
- the degree of work ⁇ is less than 1, the recrystallized grains are coarsened during the heat treatment in the next step, the tensile strength and elongation are remarkably reduced, and there is a risk of disconnection.
- the processing degree ⁇ is larger than 6, the wire drawing process becomes difficult, and there is a risk of causing a problem in terms of quality such as disconnection during the wire drawing process.
- the surface is cleaned by performing surface peeling, it may not be performed.
- the first heat treatment of the present invention is a solution heat treatment performed in order to dissolve the randomly contained Mg and Si compound in the aluminum matrix.
- the solution treatment has been performed immediately before the aging heat treatment, but in the present invention, the concentrated portion of Mg or Si is smoothed (homogenized) during the processing by performing before the second wire drawing. This leads to suppression of grain boundary segregation of the Mg and Si compound after the final aging heat treatment. That is, the first heat treatment of the present invention is a heat treatment different from the intermediate heat treatment that is normally performed during the wire drawing process in the conventional manufacturing method.
- the first heat treatment is a heat treatment in which, after heating to a predetermined temperature within a range of 480 to 620 ° C., cooling is performed at an average cooling rate of 10 ° C./s or more to a temperature of at least 150 ° C.
- the predetermined temperature during heating in the first heat treatment is higher than 620 ° C.
- the aluminum alloy wire containing the additive element is partially melted and the tensile strength, elongation, impact resistance, and bending fatigue resistance are lowered.
- the predetermined temperature is lower than 480 ° C., the solution formation cannot be sufficiently achieved, and the effect of improving the tensile strength in the subsequent aging heat treatment step cannot be sufficiently obtained, and the tensile strength is lowered. Therefore, the predetermined temperature during heating in the first heat treatment is in the range of 480 to 620 ° C., preferably in the range of 500 to 600 ° C., more preferably in the range of 520 to 580 ° C.
- the method for performing the first heat treatment may be, for example, a batch heat treatment, or a continuous heat treatment such as high-frequency heating, energization heating, or running heat.
- the wire temperature When high-frequency heating or current heating is used, the wire temperature usually rises with the passage of time because it has a structure that keeps current flowing through the wire. For this reason, if the current is kept flowing, the wire may be melted. Therefore, it is necessary to perform heat treatment in an appropriate time range. Even when running heating is used, since the annealing is performed for a short time, the temperature of the running annealing furnace is usually set higher than the wire temperature. Since heat treatment for a long time may cause the wire to melt, it is necessary to perform the heat treatment in an appropriate time range. Further, in all heat treatments, a predetermined time or more for dissolving Mg and Si compounds randomly contained in the workpiece into the aluminum matrix is required. Hereinafter, heat treatment by each method will be described.
- the continuous heat treatment by high frequency heating is a heat treatment by Joule heat generated from the wire itself by an induced current as the wire continuously passes through a magnetic field by high frequency. It includes a rapid heating and rapid cooling process, and the wire can be heat-treated under control of the wire temperature and heat treatment time. Cooling is performed by passing the wire continuously in water or in a nitrogen gas atmosphere after rapid heating.
- This heat treatment time is 0.01 to 2 s, preferably 0.05 to 1 s, more preferably 0.05 to 0.5 s.
- the continuous energization heat treatment is a heat treatment by Joule heat generated from the wire itself by passing an electric current through the wire passing continuously through the two electrode wheels. It includes a rapid heating and rapid cooling process, and the wire can be heat-treated under control of the wire temperature and heat treatment time. Cooling is performed by passing the wire continuously through water, air, or a nitrogen gas atmosphere after rapid heating. This heat treatment time is 0.01 to 2 s, preferably 0.05 to 1 s, more preferably 0.05 to 0.5 s.
- the continuous running heat treatment is a heat treatment in which a wire continuously passes through a heat treatment furnace maintained at a high temperature.
- Heat treatment can be performed by controlling the temperature in the heat treatment furnace and the heat treatment time, including rapid heating and rapid cooling processes. Cooling is performed by passing the wire continuously through water, air, or a nitrogen gas atmosphere after rapid heating.
- This heat treatment time is 0.5 to 120 s, preferably 0.5 to 60 s, more preferably 0.5 to 20 s.
- Batch type heat treatment is a method in which a wire is put into an annealing furnace and heat treated at a predetermined set temperature and set time.
- the wire itself may be heated for several tens of seconds at a predetermined temperature.
- the upper limit of the heat treatment time is not particularly limited as long as the number of crystal grains is 5 or more in the radial direction of the wire, but if the time is short, the number of crystal grains tends to be 5 or more in the radial direction of the wire. Since the productivity is good for industrial use, the heat treatment is performed within 10 hours, preferably within 6 hours.
- the solution formation becomes incomplete and the Mg 2 Si precipitates precipitated during the aging heat treatment in the subsequent process, and the tensile strength and impact resistance are reduced. , Bending fatigue resistance, and conductivity are reduced.
- the wire temperature and the annealing time are higher than the conditions defined above, the crystal grains become coarse and the partial melting (eutectic melting) of the compound phase in the aluminum alloy conductor occurs, and the tensile strength, Elongation decreases, and breakage is likely to occur when handling conductors.
- the cooling in the first heat treatment must be performed at an average cooling rate of 10 ° C./s or more up to a temperature of at least 150 ° C., which is an essential invention-specifying matter.
- the average cooling rate is less than 10 ° C./s, precipitates such as Mg and Si are generated during cooling, and the solution is not sufficiently formed, and the effect of improving the tensile strength in the subsequent aging heat treatment step This is because a sufficient tensile strength cannot be obtained.
- the average cooling rate is preferably 50 ° C./s or more, and more preferably 100 ° C./s or more.
- the cooling in the first heat treatment of the present invention is preferably performed by heating the aluminum alloy wire after the first wire drawing to a predetermined temperature and then passing it through water in any of the heat treatment methods described above.
- the cooling rate cannot be measured accurately. Therefore, in such a case, in any heat treatment method, the average cooling rate by water cooling after heating is estimated after the aluminum alloy wire is cooled to the water temperature (about 20 ° C.) immediately after the water cooling, and then each heat treatment is performed.
- the cooling rate calculated as follows was used as the average cooling rate. That is, in the batch type heat treatment, from the viewpoint that it is important to keep the cooling rate at 150 ° C.
- the temperature is 100 ° C./s or more because the mechanism is such that after heating, the aluminum alloy wire is cooled by water after passing through several meters at a linear speed of 100 to 1500 m / min.
- the temperature is 100 ° C./s or more
- the wire speed of the aluminum alloy wire is 10 to 500 m / min immediately after heating.
- the room temperature about approx. If it is calculated that the air is cooled to 20 ° C), the section length during air cooling is 10m, the cooling start temperature is 500 ° C, and the cooling is about 6 to 292 ° C / s. To become. Therefore, a cooling rate of 10 ° C./s or more is sufficiently possible.
- any of the heat treatment methods may be rapidly cooled to at least 150 ° C. from the viewpoint of achieving the purpose of the solution heat treatment.
- the cooling in the first heat treatment is performed at an average cooling rate of 20 ° C./s or more up to a temperature of at least 250 ° C., which exhibits the effect of improving the tensile strength in the subsequent aging heat treatment step by suppressing the precipitation of Mg and Si. This is preferable. Since the peak of the precipitation temperature zone of Mg and Si is located at 300 to 400 ° C., in order to suppress the precipitation of Mg and Si during cooling, it is preferable to increase the cooling rate at least at the temperature.
- the working degree ⁇ is preferably in the range of 1 to 6.
- the degree of work ⁇ affects the formation and growth of recrystallized grains. If the degree of work ⁇ is less than 1, the recrystallized grains tend to be coarsened during the heat treatment in the next step, and the tensile strength and elongation tend to be significantly reduced. This is because it tends to cause problems in terms of quality, such as disconnection during wire drawing.
- Second heat treatment A second heat treatment is performed on the cold-drawn workpiece.
- the second heat treatment is a heat treatment different from the first heat treatment described above and the aging heat treatment described later. Similar to the first heat treatment, the second heat treatment may be performed by batch annealing, or may be performed by continuous annealing such as high-frequency heating, energization heating, or running heat. However, it needs to be done in a short time. When heat treatment is performed for a long time, precipitation of Mg and Si occurs, and the effect of improving the tensile strength in the subsequent aging heat treatment step cannot be obtained, and the tensile strength is lowered.
- the second heat treatment needs to be performed by a manufacturing method in which the temperature rising process from 150 ° C., holding, and the temperature lowering process to 150 ° C. can be performed within 2 minutes. Therefore, in the case of batch-type annealing, which is usually carried out by holding for a long time, it is practically difficult to carry out, and continuous annealing such as high-frequency heating, energization heating, and running heat is preferable.
- the second heat treatment is not a solution heat treatment like the first heat treatment but a heat treatment performed to regain the flexibility of the wire and improve the elongation.
- the heating temperature of the second heat treatment is set to be 300 ° C. or higher and lower than 480 ° C. If the heating temperature of the second heat treatment is less than 300 ° C., there is a tendency that recrystallization is not performed and the effect of improving the elongation is not obtained, and if the heating temperature is 480 ° C. or more, the concentration of Mg or Si element is high. This is because there is a tendency that tensile strength, elongation, impact resistance, and bending fatigue resistance tend to decrease.
- the heating temperature of the second heat treatment is preferably 300 to 450 ° C., more preferably 325 to 450 ° C. Further, if the heating time of the second heat treatment is 2 minutes or more, a 0.5 to 5.0 ⁇ m Mg 2 Si compound is likely to be formed, and the dispersion density of the 0.5 to 5.0 ⁇ m Mg 2 Si compound is increased. Since it tends to exceed 3.0 ⁇ 10 ⁇ 3 pieces / ⁇ m 2 , it is set to less than 2 minutes.
- the cooling in the second heat treatment must be performed at an average cooling rate of 9 ° C./s or higher up to a temperature of at least 150 ° C. as an essential invention-specifying matter.
- the average cooling rate is less than 9 ° C./s, precipitates such as Mg 2 Si including Mg 2 Si are generated during cooling, and the effect of improving the tensile strength in the subsequent aging heat treatment step is limited. This is because sufficient tensile strength tends not to be obtained.
- the average cooling rate is preferably 50 ° C./s or more, and more preferably 100 ° C./s or more.
- the effect of improving the tensile strength in the subsequent aging heat treatment step by suppressing the precipitation of Mg and Si is exhibited.
- the peak of the precipitation temperature zone of Mg and Si is located at 300 to 400 ° C., in order to suppress the precipitation of Mg and Si during cooling, it is preferable to increase the cooling rate at least at the temperature.
- the aging heat treatment is performed in order to precipitate acicular Mg 2 Si precipitates.
- the heating temperature in the aging heat treatment is preferably 140 to 250 ° C. If the heating temperature is less than 140 ° C., needle-like Mg 2 Si precipitates cannot be sufficiently precipitated, and the strength, impact resistance, bending fatigue resistance and electrical conductivity tend to be insufficient. On the other hand, when the heating temperature is higher than 250 ° C., the size of the Mg 2 Si precipitate increases, and thus the conductivity increases, but the strength, impact resistance and bending fatigue resistance tend to be insufficient.
- the heating temperature in the aging heat treatment is preferably 160 to 200 ° C.
- the heating time varies depending on the temperature. Heating at a low temperature for a long time and at a high temperature for a short time is preferable for improving strength, impact resistance, and bending fatigue resistance. Considering productivity, the short time is good, preferably 15 hours or shorter, more preferably 10 hours or shorter.
- the cooling in the aging heat treatment is preferably as fast as possible in order to prevent variations in characteristics. However, when cooling cannot be performed quickly due to the manufacturing process, the aging conditions can be appropriately set taking into account the increase or decrease in acicular Mg 2 Si precipitates during cooling.
- the wire diameter of the aluminum alloy conductor of the present invention is not particularly limited and can be appropriately determined according to the application, but is 0.1 to 0.5 mm ⁇ for a fine wire and 0 for a medium thin wire. .8 to 1.5 mm ⁇ is preferable.
- One of the advantages of the aluminum alloy conductor of the present invention is that the aluminum alloy wire can be used as a thin single wire, but it can also be used as an aluminum alloy twisted wire obtained by bundling a plurality of wires.
- the steps [1] to [8] constituting the manufacturing method of the invention after the aluminum alloy wires obtained by sequentially performing the steps [1] to [6] are bundled and twisted, [7 The second heat treatment and [8] aging heat treatment may be performed.
- the present invention it is possible to perform a homogenization heat treatment as performed by a conventional method after continuous casting and rolling.
- the homogenization heat treatment precipitates of the additive elements (mainly Mg—Si compounds) can be uniformly dispersed, so that a uniform crystal structure can be easily obtained in the subsequent first heat treatment. Improvements in elongation, impact resistance, and bending fatigue resistance can be obtained more stably.
- the homogenization heat treatment is preferably performed at a heating temperature of 450 ° C. to 600 ° C. and a heating time of 1 to 10 hours, more preferably 500 to 600 ° C.
- the cooling in the homogenization heat treatment is preferably slow cooling at an average cooling rate of 0.1 to 10 ° C./min from the viewpoint of easily obtaining a uniform compound.
- the aluminum alloy conductor of the present invention has an impact absorption energy of 5 J / mm 2 or more, and can achieve excellent impact resistance. Further, the number of repetitions until breakage measured by a bending fatigue test is 200,000 times or more, and excellent bending fatigue resistance characteristics can be achieved.
- the aluminum alloy conductor of the present invention can be used as an aluminum alloy wire or an aluminum alloy twisted wire obtained by twisting a plurality of aluminum alloy wires, and further, an aluminum alloy wire or an aluminum alloy twisted wire Can also be used as a coated electric wire having a coating layer on the outer periphery of the wire harness, and in addition, a wire harness (assembled electric wire) comprising a coated electric wire and a terminal attached to the end of the coated electric wire from which the coating layer has been removed It is also possible to use as
- a first heat treatment was performed on the processed material subjected to the first wire drawing under the conditions shown in Tables 3 and 4, and the second wire drawing was further performed to a wire diameter of 0.31 mm ⁇ .
- the second heat treatment was performed under the conditions shown in Tables 3 and 4.
- the wire temperature was measured by winding a thermocouple around the wire.
- continuous energization heat treatment it is difficult to measure at the part where the temperature of the wire becomes the highest because of the equipment. The temperature was measured, and the maximum temperature reached was calculated in consideration of Joule heat and heat dissipation.
- the wire temperature near the exit of the heat treatment section was measured.
- the dispersion density of the Mg 2 Si compound is calculated by using the sample thickness of the thin film as a reference thickness of 0.15 ⁇ m. If the sample thickness is different from the reference thickness, the sample thickness is converted into the reference thickness, that is, (reference thickness / sample thickness) is applied to the dispersion density calculated based on the photographed photo, Dispersion density can be calculated. In this example and the comparative example, the sample thickness was set to about 0.15 ⁇ m for all samples by the FIB method.
- the " ⁇ " as the dispersion density of the Mg 2 Si compound is in a suitable range, 0 ⁇
- (E) Impact absorption energy This is an index of how much impact the aluminum alloy conductor can withstand, and was calculated by (position energy of weight) / (cross-sectional area of the aluminum alloy conductor) immediately before the aluminum alloy conductor is disconnected. Specifically, a weight was attached to one end of the aluminum alloy conductor wire, and the weight was freely dropped from a height of 300 mm. The weight was gradually changed to a heavy one, and the shock absorption energy was calculated from the weight of the weight just before the disconnection. It can be said that the greater the shock absorption energy, the higher the shock absorption. The impact absorption energy was set to 5 J / mm 2 or more as an acceptable level.
- the aluminum alloy wires of Invention Examples 1 to 57 all have the same level of tensile strength, elongation, and electrical conductivity as conventional products (the aluminum alloy wire described in Patent Document 1, equivalent to Comparative Example 12), as well as impact resistance and Excellent bending fatigue resistance.
- the aluminum alloy wires of Comparative Examples 1 to 19 all had a low number of repetitions until breakage of 180,000 times or less, and were inferior in bending fatigue resistance. Except for Comparative Examples 10 and 16, the impact resistance was also poor. Further, all of Comparative Examples 5 to 9 were disconnected during the wire drawing process.
- the aluminum alloy conductor of the present invention is based on the premise that an aluminum alloy containing Mg and Si is used, and suppresses grain boundary segregation caused by the Mg component and the Si component. Even when used as an extra fine wire, the impact resistance and bending fatigue resistance are improved while ensuring the same level of strength, elongation and conductivity as the conventional product (aluminum alloy wire described in Patent Document 1). It is possible to provide an aluminum alloy conductor, an aluminum alloy twisted wire, a covered electric wire, a wire harness used as a conductor of an electric wiring body, and a method for producing an aluminum alloy conductor, which is mounted on a moving body.
- the aluminum alloy conductor of the present invention has high tensile strength, it is possible to make the wire diameter thinner than conventional wires, and wiring such as doors, trunks, and bonnets that require high bending fatigue resistance is required. Also, it can be suitably used.
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Abstract
Description
(1)Mg:0.1~1.0質量%、Si:0.1~1.0質量%、Fe:0.01~1.40質量%、Ti:0.000~0.100質量%、B:0.000~0.030質量%、Cu:0.00~1.00質量%、Ag:0.00~0.50質量%、Au:0.00~0.50質量%、Mn:0.00~1.00質量%、Cr:0.00~1.00質量%、Zr:0.00~0.50質量%、Hf:0.00~0.50質量%、V:0.00~0.50質量%、Sc:0.00~0.50質量%、Co:0.00~0.50質量%、Ni:0.00~0.50質量%、残部:Alおよび不可避不純物である組成を有し、粒子径0.5~5.0μmのMg2Si化合物の分散密度が3.0×10-3個/μm2以下であり、母相の結晶粒同士の結晶粒界におけるSiおよびMgの濃度がいずれも2.00質量%以下であることを特徴とするアルミニウム合金導体。
(2)前記化学組成が、Ti:0.001~0.100質量%およびB:0.001~0.030質量%からなる群から選択された1種または2種を含有する上記(1)に記載のアルミニウム合金導体。
(3)前記化学組成が、Cu:0.01~1.00質量%、Ag:0.01~0.50質量%、Au:0.01~0.50質量%、Mn:0.01~1.00質量%、Cr:0.01~1.00質量%、Zr:0.01~0.50質量%、Hf:0.01~0.50質量%、V:0.01~0.50質量%、Sc:0.01~0.50質量%、Co:0.01~0.50質量%およびNi:0.01~0.50質量%からなる群から選択された1種または2種以上を含有する上記(1)または(2)に記載のアルミニウム合金導体。
(4)Fe、Ti、B、Cu、Ag、Au、Mn、Cr、Zr、Hf、V、Sc、Co、Niの含有量の合計が0.01~2.00質量%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)衝撃吸収エネルギーが5J/mm2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)屈曲疲労試験によって測定した破断までの繰返回数が20万回以上である上記(1)~(5)のいずれか1項に記載のアルミニウム合金導体。
(7)素線径が0.1~0.5mmであるアルミニウム合金線である上記(1)~(6)のいずれか1項に記載のアルミニウム合金導体。
(8)上記(7)に記載のアルミニウム合金線を複数本撚り合わせて得られるアルミニウム合金撚線。
(9)上記(7)に記載のアルミニウム合金線または上記(8)に記載のアルミニウム合金撚線の外周に被覆層を有する被覆電線。
(10)上記(9)に記載の被覆電線と、該被覆電線の、前記被覆層を除去した端部に装着された端子とを具えるワイヤーハーネス。
(11)溶解、鋳造後に、熱間加工を経て荒引線を形成し、その後、第1伸線加工、第1熱処理、第2伸線加工、第2熱処理および時効熱処理の各工程を順次行うことを含むアルミニウム合金導体の製造方法であって、第1熱処理は、480~620℃の範囲内の所定温度まで加熱した後、少なくとも150℃の温度までは10℃/s以上の平均冷却速度で冷却し、前記第2熱処理は、300℃以上480℃未満の範囲内の所定温度において2分間未満加熱した後、少なくとも150℃の温度までは9℃/s以上の平均冷却速度で冷却することを特徴とする上記(1)~(7)のいずれか1項に記載のアルミニウム合金導体の製造方法。
(1)化学組成
<Mg:0.10~1.00質量%>
Mg(マグネシウム)は、アルミニウム母材中に固溶して強化する作用を有すると共に、その一部はSiと化合して析出物を形成して引張強度、耐屈曲疲労特性および耐熱性を向上させる作用を有する元素である。しかしながら、Mg含有量が0.10質量%未満だと、上記作用効果が不十分であり、また、Mg含有量が1.00質量%を超えると、結晶粒界にMg濃化部分を形成する可能性が高まり、引張強度、伸び、耐屈曲疲労特性が低下するとともに、Mg元素の固溶量が多くなることによって導電率も低下する。したがって、Mg含有量は0.10~1.00質量%とする。なお、Mg含有量は、高強度を重視する場合には0.50~1.00質量%にすることが好ましく、また、導電率を重視する場合には0.10~0.50質量%とすることが好ましく、このような観点から総合的に0.30~0.70質量%が好ましい。
Si(ケイ素)は、Mgと化合して析出物を形成して引張強度、耐屈曲疲労特性、及び耐熱性を向上させる作用を有する元素である。Si含有量が0.10質量%未満だと、上記作用効果が不十分であり、また、Si含有量が1.00質量%を超えると、結晶粒界にSi濃化部分を形成する可能性が高まり、引張強度、伸び、耐屈曲疲労特性が低下するとともに、Si元素の固溶量が多くなることによって導電率も低下する。したがって、Si含有量は0.10~1.00質量%とする。なお、Si含有量は、高強度を重視する場合には0.50~1.00質量%にすることが好ましく、また、導電率を重視する場合には0.10~0.50質量%とすることが好ましく、このような観点から総合的に0.30~0.70質量%が好ましい。
Fe(鉄)は、主にAl-Fe系の金属間化合物を形成することによって結晶粒の微細化に寄与すると共に、引張強度および耐屈曲疲労特性を向上させる元素である。Feは、Al中に655℃で0.05質量%しか固溶できず、室温では更に少ないため、Al中に固溶できない残りのFeは、Al-Fe、Al-Fe-Si、Al-Fe-Si-Mgなどの金属間化合物として晶出又は析出する。この金属間化合物は、結晶粒の微細化に寄与すると共に、引張強度および耐屈曲疲労特性を向上させる。また、Feは、Al中に固溶したFeによっても引張強度を向上させる作用を有する。Fe含有量が0.01質量%未満だと、これらの作用効果が不十分であり、また、Fe含有量が1.40質量%超えだと、晶出物または析出物の粗大化により伸線加工性が悪くなり、その結果、目的とする耐屈曲疲労特性が得られなくなる他、導電率も低下する。したがって、Fe含有量は0.01~1.40質量%とし、好ましくは0.15~0.90質量%、更に好ましくは0.15~0.45質量%とする。
Tiは、溶解鋳造時の鋳塊の組織を微細化する作用を有する元素である。鋳塊の組織が粗大であると、鋳造において鋳塊割れや線材加工工程において断線が発生して工業的に望ましくない。Ti含有量が0.001質量%未満であると、上記作用効果を十分に発揮することができず、また、Ti含有量が0.100質量%超えだと導電率が低下する傾向があるからである。したがって、Ti含有量は0.001~0.100質量%とし、好ましくは0.005~0.050質量%、より好ましくは0.005~0.030質量%とする。
Bは、Tiと同様、溶解鋳造時の鋳塊の組織を微細化する作用を有する元素である。鋳塊の組織が粗大であると、鋳造において鋳塊割れや線材加工工程において断線が発生しやすくなるため工業的に望ましくない。B含有量が0.001質量%未満であると、上記作用効果を十分に発揮することができず、また、B含有量が0.030質量%超えだと導電率が低下する傾向がある。したがって、B含有量は0.001~0.030質量%とし、好ましくは0.001~0.020質量%、より好ましくは0.001~0.010質量%とする。
Cu、Ag、Au、Mn、Cr、Zr、Hf、V、Sc、CoおよびNiは、いずれも結晶粒を微細化する作用を有する元素であり、さらに、Cu、AgおよびAuは、粒界に析出することで粒界強度を高める作用も有する元素であって、これらの元素の少なくとも1種を0.01質量%以上含有していれば、上述した作用効果が得られ、引張強度、伸び、耐屈曲疲労特性を向上させることができる。一方、Cu、Ag、Au、Mn、Cr、Zr、Hf、V、Sc、CoおよびNiの含有量のいずれかが、それぞれ上記の上限値を超えると、該元素を含有する化合物が粗大になり、伸線加工性を劣化させるため、断線が生じやすく、また、導電率が低下する傾向がある。したがって、Cu、Ag、Au、Mn、Cr、Zr、Hf、V、Sc、CoおよびNiの含有量の範囲は、それぞれ上記の範囲とした。
上述した成分以外の残部はAl(アルミニウム)および不可避不純物である。ここでいう不可避不純物は、製造工程上、不可避的に含まれうる含有レベルの不純物を意味する。不可避不純物は、含有量によっては導電率を低下させる要因にもなりうるため、導電率の低下を加味して不可避不純物の含有量をある程度抑制することが好ましい。不可避不純物として挙げられる成分としては、例えば、Ga、Zn、Bi、Pbなどが挙げられる。
本発明のアルミニウム合金導体は、アルミニウム母相の結晶粒内に存在する特定の大きさのMg2Si化合物の密度を規定する。0.5~5.0μmのMg2Si化合物は、主に、後述する第1熱処理が480℃未満で2分以上熱処理された場合や、第1熱処理の冷却速度が10℃/s未満の場合、第2熱処理温度が480℃未満で2分間以上熱処理された場合、第2熱処理の冷却速度が9℃/s未満の場合などに形成する。0.5~5.0μmのMg2Si化合物の分散密度が3.0×10-3個/μm2を超えて形成すると、時効熱処理の際に形成する針状のMg2Si析出物が少なくなり、引張強度や、耐衝撃性、耐屈曲疲労特性、導電率の向上幅が小さくなる。0.5~5μmのMg2Si化合物の分散密度は、小さいほど好ましい。すなわち、0に近いほど好ましい。また、Mg2Si化合物に限らず、Mg-Si系を主成分とする化合物の密度が上記の規定範囲外にあっても時効熱処理の際に形成する針状のMg2Si析出物が少なくなり、引張強度や耐衝撃性、耐屈曲疲労特性、導電率の向上幅が小さくなるため、Mg-Si系を主成分とする化合物の密度も同様に上記の規定範囲にて設定される。
本発明のアルミニウム合金導体は、アルミニウム母相の結晶粒界におけるSi元素とMg元素の濃化部分でのそれぞれ濃度を以下のように規定することにより、従来品(特許文献1記載のアルミニウム合金線)と同等レベルの強度、伸びおよび導電率を確保しつつ、耐衝撃性および耐屈曲疲労特性を向上させることができる。
本発明のアルミニウム合金導体は、[1]溶解、[2]鋳造、[3]熱間加工(溝ロール加工など)、[4]第1伸線加工、[5]第1熱処理(溶体化熱処理)、[6]第2伸線加工、[7]第2熱処理、および[8]時効熱処理の各工程を順次行うことを含む製造方法によって製造することができる。なお、第2熱処理前後、または時効熱処理の後に、撚り線とする工程や電線に樹脂被覆を行う工程を設けてもよい。以下、[1]~[8]の工程について説明する。
溶解は、上述したアルミニウム合金組成になるように各成分の分量を調整して溶製する。
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鋳造し、連続して圧延を行い、例えば直径5~13mmφの適宜の太さの棒材とする。このときの鋳造時の冷却速度は、Fe系晶出物の粗大化の防止とFeの強制固溶による導電率低下の防止の観点から、好ましくは1~20℃/sであるが、これに制限されるものではない。鋳造及び熱間圧延は、ビレット鋳造及び押出法などにより行ってもよい。
次いで、表面の皮むきを実施して、例えば直径5~12.5mmφの適宜の太さの棒材とし、これを冷間で伸線加工する。加工度ηは、1~6の範囲であることが好ましい。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。加工度ηが1未満だと、次工程の熱処理時、再結晶粒が粗大化し、引張強度及び伸びが著しく低下し、断線の原因になるおそれがある。また、加工度ηが6よりも大きいと、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おそれがあるからである。表面の皮むきは、行うことによって表面の清浄化がなされるが、行わなくてもよい。
冷間伸線した加工材に第1熱処理を施す。本発明の第1熱処理は、ランダムに含有されているMgとSiの化合物をアルミニウム母相中に溶け込ませるために行う溶体化熱処理である。溶体化処理は、従来、時効熱処理の直前に行っていたが、本発明では、第2伸線加工前に行うことによって、加工中にMgやSiの濃化部分をならす(均質化する)ことができ、最終的な時効熱処理後でのMgとSiの化合物の粒界偏析の抑制につながる。つまり、本発明の第1熱処理は、従来の製造方法において伸線加工途中で通常行われる中間熱処理とは異なる熱処理である。第1熱処理は、具体的には、480~620℃の範囲内の所定温度まで加熱した後、少なくとも150℃の温度までは10℃/s以上の平均冷却速度で冷却する熱処理である。第1熱処理の加熱時の所定温度が620℃よりも高いと、添加元素を含んでいるアルミニウム合金線は部分的に溶融してしまい、引張強度、伸び、耐衝撃性および耐屈曲疲労特性が低下し、また、所定温度が480℃よりも低いと、溶体化が十分に達成できずに、その後の時効熱処理工程での引張強度の向上効果が十分に得られず、引張強度が低下する。したがって、第1熱処理における加熱時の所定温度は480~620℃の範囲とし、好ましくは500~600℃の範囲、更に好ましくは520~580℃の範囲とする。
上記第1熱処理の後、さらに冷間で伸線加工を施す。この際の加工度ηは1~6の範囲が好ましい。加工度ηは、再結晶粒の形成及び成長に影響を及ぼす。加工度ηが1よりも小さいと、次工程の熱処理時、再結晶粒が粗大化し、引張強度及び伸びが著しく低下する傾向があり、また、加工度ηが6よりも大きいと、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傾向があるからである。
冷間伸線した加工材に第2熱処理を行う。第2熱処理は、前述した第1熱処理や後述する時効熱処理とは異なった熱処理である。第2熱処理は、第1熱処理と同様、バッチ式焼鈍で行っても、また、高周波加熱、通電加熱、走間加熱などの連続焼鈍で行ってもよい。しかし、短時間で行う必要がある。長時間熱処理を施すと、MgおよびSiの析出が生じてしまい、その後の時効熱処理工程での引張強度の向上効果が得られず、引張強度が低下するためである。すなわち、第2熱処理は150℃からの昇温、保持、150℃までの降温過程を2分以内で行える製法で施す必要がある。そのため通常長時間の保持にて実施されるバッチ式焼鈍の場合は現実的に実施が難しく、好ましくは高周波加熱、通電加熱、走間加熱などの連続焼鈍である。
次いで、時効熱処理を施す。時効熱処理は、針状のMg2Si析出物を析出させるために行う。時効熱処理における加熱温度は、好ましくは140~250℃である。前記加熱温度が140℃未満であると、針状のMg2Si析出物を十分に析出させることができず、強度、耐衝撃性、耐屈曲疲労特性および導電率が不足しがちである。また、前記加熱温度が250℃よりも高いと、Mg2Si析出物のサイズが大きくなるため、導電率は上昇するが、強度、耐衝撃性および耐屈曲疲労特性が不足しがちである。時効熱処理における加熱温度は、耐衝撃性や高耐屈曲疲労特性を重視する場合には、好ましくは160~200℃であり、また、導電率を重視する場合には、好ましくは180~220℃である。なお、加熱時間は、温度によって最適な時間が変化する。低温では長時間、高温では短時間の加熱が強度、耐衝撃性、耐屈曲疲労特性を向上させる上で好ましい。生産性を考慮すると短時間が良く、好ましくは15時間以下、更に好ましくは10時間以下である。なお、時効熱処理における冷却は、特性のバラつきを防止するために、可能な限り冷却速度を速くすることが好ましい。しかし、製造工程上、速く冷却できない場合は、冷却中に針状のMg2Si析出物の増加や減少が起こることも考慮に入れて時効条件を適宜設定することができる。
Mg、Si、Fe及びAlと、選択的に添加するTi、B、Cu、Ag、Au、Mn、Cr、Zr、Hf、V、Sc、Co、Niを、表1および表2に示す含有量(質量%)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い、約9.5mmφの棒材とした。このときの鋳造時の冷却速度は約15℃/sとした。これを所定の加工度が得られるように第1伸線加工を施した。次に、この第1伸線加工を施した加工材に、表3および表4に示す条件で第1熱処理を施し、さらに0.31mmφの線径まで第2伸線加工を行った。次に、表3および表4に示す条件で第2熱処理を施した。第1及び第2熱処理とも、バッチ式熱処理では、線材に熱電対を巻きつけて線材温度を測定した。連続通電熱処理では、線材の温度が最も高くなる部分での測定が設備上困難であるため、ファイバ型放射温度計(ジャパンセンサ社製)で線材の温度が最も高くなる部分よりも手前の位置にて温度を測定し、ジュール熱と放熱を考慮して最高到達温度を算出した。高周波加熱および連続走間熱処理では、熱処理区間出口付近の線材温度を測定した。第2熱処理後に、表3及び表4に示す条件で時効熱処理を施し、アルミニウム合金線を製造した。なお、比較例12は、特許文献1記載の表1の試料No.2の組成を有し、同文献で開示するのと同等の製法に倣ってアルミニウム合金線を製造したので、併せて評価した。
実施例及び比較例の線材を集束イオンビーム(FIB)法にて薄膜にし、透過電子顕微鏡(TEM)を用いて、任意の範囲を観察した。Mg2Si化合物は、EDXにて組成分析を行い、化合物種を同定した。また、Mg2Si化合物は、板状の化合物として観察されたため、撮影された写真から板状化合物の辺にあたる部分が0.5~5.0μmの化合物をカウントした。化合物が測定範囲外にまたがるとき、化合物が0.5μm以上観察できていれば、化合物数にカウントした。Mg2Si化合物の分散密度は20個以上をカウントできる範囲を設定して、Mg2Si化合物の分散密度(個/μm2)=Mg2Si化合物の個数(個)/カウント対象範囲(μm2)の式を用いて算出した。カウント対象範囲は場合によっては複数枚の写真を用いた。20個以上カウントできないほど化合物が少ない場合は、1000μm2を指定してその範囲の分散密度を算出した。
SiおよびMgの濃度は、光学顕微鏡およびEPMAを用いて測定した。なお、SiおよびMgの濃度の測定は、光学顕微鏡や電子顕微鏡、電子プローブマイクロアナライザー(EPMA)を用いて行う。まず、結晶粒コントラストが見えるように試料準備をした後、光学顕微鏡等にて結晶粒及び結晶粒界の観察を行いながら、観察視野内において例えば120μm×120μmの正方形の頂点4箇所に圧痕をつけて観察場所を特定する。次に、EPMAにて、4箇所の圧痕を含む120μm×120μmの視野にて面分析を行い、本発明で規定する1μm以上の長さの線状のMgまたはSiの濃化部分と、化合物起因の粒状のMgまたはSiの濃化部分を区別し、本発明では、前記線状の濃化部分がある場合には、その線状の濃化部分を最初に観察した光学顕微鏡等の観察結果を参考に結晶粒界とし、化合物起因の粒状の濃化部分は測定対象外とした。次に、結晶粒界の濃化部分を横切るように線分析を行い、前記線状の濃化部分のSi元素とMg元素の最大濃度を測定した。このような測定方法により線状の濃化部分を任意に10箇所選択して濃度を測定した。1視野にて10箇所が測定できない場合は、別の視野にて同様に観察して合計10箇所の線状の濃化部分を測定した。なお、線分析の長さは50μmとした。一方、前記線状の濃化部分が観察されない場合には、結晶粒界におけるMgまたはSiのそれぞれの濃度は0質量%とみなして線分析は行わなかった。表3及び表4には、線分析の全ての範囲においてSiおよびFMgの濃度がそれぞれ2.00質量%以下である場合または前記線状の濃化部分が観察されない場合については、粒界偏析が生じていないあるいは粒界偏析の程度が低いため合格として「○」と記載し、また、SiおよびMgの濃度がそれぞれ2.00質量%超えである場合は、粒界偏析が生じているため不合格として「×」と記載した。
JIS Z 2241に準じて各3本ずつの供試材(アルミニウム合金線)について引張試験を行い、その平均値を求めた。引張強度は電線と端子の接続部における圧着部の引張強度を保つため、また、車体への取付け作業時に不意に負荷される荷重に耐えられるためにも150MPa以上を合格レベルとした。伸びは5%以上を合格とした。
長さ300mmの試験片を20℃(±0.5℃)に保持した恒温漕中で、四端子法を用いて各3本ずつの供試材(アルミニウム合金線)について比抵抗を測定し、その平均導電率を算出した。端子間距離は200mmとした。導電率は特に限定しないが、40%IACS以上を合格レベルとした。
アルミニウム合金導体がどれほどの衝撃に耐えられるかの指標であり、アルミニウム合金導体が断線する直前の(錘の位置エネルギー)/(アルミニウム合金導体の断面積)で算出した。具体的には、アルミニウム合金導体線の一方の端に錘を付け、錘を300mmの高さから自由落下させた。錘を重いものに順次変えていき、断線する直前の錘の重さから衝撃吸収エネルギーを計算した。衝撃吸収エネルギーが大きい程、高い衝撃吸収性を有しているといえる。衝撃吸収エネルギーは、5J/mm2以上を合格レベルとした。
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、線材の線径と曲げ冶具の曲率半径により決定することができるため、線材の線径と曲げ冶具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、破断までの繰返回数を測定した。本発明では、破断までの繰返回数は、20万回以上を合格とした。
Claims (11)
- Mg:0.1~1.0質量%、Si:0.1~1.0質量%、Fe:0.01~1.40質量%、Ti:0.000~0.100質量%、B:0.000~0.030質量%、Cu:0.00~1.00質量%、Ag:0.00~0.50質量%、Au:0.00~0.50質量%、Mn:0.00~1.00質量%、Cr:0.00~1.00質量%、Zr:0.00~0.50質量%、Hf:0.00~0.50質量%、V:0.00~0.50質量%、Sc:0.00~0.50質量%、Co:0.00~0.50質量%、Ni:0.00~0.50質量%、残部:Alおよび不可避不純物である組成を有し、
粒子径0.5~5.0μmのMg2Si化合物の分散密度が3.0×10-3個/μm2以下であり、
母相の結晶粒同士の結晶粒界におけるSiおよびMgの濃度がいずれも2.00質量%以下であることを特徴とするアルミニウム合金導体。 - 前記化学組成が、Ti:0.001~0.100質量%およびB:0.001~0.030質量%からなる群から選択された1種または2種を含有する請求項1に記載のアルミニウム合金導体。
- 前記化学組成が、Cu:0.01~1.00質量%、Ag:0.01~0.50質量%、Au:0.01~0.50質量%、Mn:0.01~1.00質量%、Cr:0.01~1.00質量%、Zr:0.01~0.50質量%、Hf:0.01~0.50質量%、V:0.01~0.50質量%、Sc:0.01~0.50質量%、Co:0.01~0.50質量%、およびNi:0.01~0.50質量%からなる群から選択された1種または2種以上を含有する請求項1または2に記載のアルミニウム合金導体。
- Fe、Ti、B、Cu、Ag、Au、Mn、Cr、Zr、Hf、V、Sc、Co、Niの含有量の合計が0.01~2.00質量%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。
- 衝撃吸収エネルギーが5J/mm2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。
- 屈曲疲労試験によって測定した破断までの繰返回数が20万回以上である請求項1~5のいずれか1項に記載のアルミニウム合金導体。
- 素線の直径が0.1~0.5mmであるアルミニウム合金線である請求項1~6のいずれか1項に記載のアルミニウム合金導体。
- 請求項7に記載のアルミニウム合金線を複数本撚り合わせて得られるアルミニウム合金撚線。
- 請求項7に記載のアルミニウム合金線または請求項8に記載のアルミニウム合金撚線の外周に被覆層を有する被覆電線。
- 請求項9に記載の被覆電線と、該被覆電線の、前記被覆層を除去した端部に装着された端子とを具えるワイヤーハーネス。
- 溶解、鋳造後に、熱間加工を経て荒引線を形成し、その後、第1伸線加工、第1熱処理、第2伸線加工、第2熱処理および時効熱処理の各工程を順次行うことを含むアルミニウム合金導体の製造方法であって、
前記第1熱処理は、480~620℃の範囲内の所定温度まで加熱した後、少なくとも150℃の温度までは10℃/s以上の平均冷却速度で冷却し、
前記第2熱処理は、300℃以上480℃未満の範囲内の所定温度において2分間未満加熱した後、少なくとも150℃の温度までは9℃/s以上の平均冷却速度で冷却す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の製造方法。
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CN201380053482.0A CN104781433B (zh) | 2013-03-29 | 2013-11-15 | 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 |
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JP2015096645A (ja) * | 2013-11-15 | 2015-05-21 | 古河電気工業株式会社 | アルミニウム合金導体、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 |
US20170243667A1 (en) * | 2014-12-05 | 2017-08-24 | Yazaki Corporation | Aluminum alloy electrical wire and wire harness using same |
WO2016088825A1 (ja) * | 2014-12-05 | 2016-06-09 | 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ワイヤーハーネス |
JP2016108603A (ja) * | 2014-12-05 | 2016-06-20 | 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ワイヤーハーネス |
JP2016108617A (ja) * | 2014-12-05 | 2016-06-20 | 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、並びにアルミニウム合金線材およびアルミニウム合金撚線の製造方法 |
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WO2016199564A1 (ja) * | 2015-06-12 | 2016-12-15 | 株式会社オートネットワーク技術研究所 | アルミニウム合金線、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 |
US10370743B2 (en) | 2015-06-12 | 2019-08-06 | Autonetworks Technologies, Ltd. | Aluminum alloy wire, aluminum alloy twisted wire, covered wire, and wiring harness |
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JPWO2018079049A1 (ja) * | 2016-10-31 | 2019-09-12 | 住友電気工業株式会社 | アルミニウム合金線、アルミニウム合金撚線、被覆電線、及び端子付き電線 |
JPWO2018079050A1 (ja) * | 2016-10-31 | 2019-09-12 | 住友電気工業株式会社 | アルミニウム合金線、アルミニウム合金撚線、被覆電線、及び端子付き電線 |
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JP7137759B2 (ja) | 2016-10-31 | 2022-09-15 | 住友電気工業株式会社 | アルミニウム合金線、アルミニウム合金撚線、被覆電線、及び端子付き電線 |
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JP2020050901A (ja) * | 2018-09-26 | 2020-04-02 | 矢崎総業株式会社 | アルミニウム合金電線の製造方法、アルミニウム合金電線及びワイヤーハーネス |
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Also Published As
Publication number | Publication date |
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EP2896706B1 (en) | 2017-09-06 |
JP5607855B1 (ja) | 2014-10-15 |
JPWO2014155817A1 (ja) | 2017-02-16 |
EP2896706A4 (en) | 2016-08-03 |
CN104781433A (zh) | 2015-07-15 |
CN107254611B (zh) | 2019-04-02 |
EP3266891B1 (en) | 2019-08-14 |
CN107254611A (zh) | 2017-10-17 |
CN104781433B (zh) | 2017-07-07 |
KR20150140710A (ko) | 2015-12-16 |
EP2896706A1 (en) | 2015-07-22 |
EP3266891A1 (en) | 2018-01-10 |
KR101898321B1 (ko) | 2018-09-12 |
US9324471B2 (en) | 2016-04-26 |
US20150279499A1 (en) | 2015-10-01 |
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