JP6562087B2 - Wire harness and method for manufacturing wire harness - Google Patents

Description

  The present invention relates to an aluminum alloy for conductive wires, a conductive wire, and a method for manufacturing a wire harness.

  As a material used for the conductive wire, an aluminum alloy as disclosed in Patent Document 1 is known.

JP 2005-336549 A

  In an aluminum alloy as disclosed in Patent Document 1, it is necessary to strictly control the casting temperature during casting in order to suppress a casting defect because the temperature range of the solid-liquid coexistence region is narrow.

  The aspect of this invention aims at providing the manufacturing method of the aluminum alloy for conductive wires in which a casting defect is suppressed, a conductive wire, and a wire harness.

  The aluminum alloy for conductive wires according to an embodiment of the present invention includes 0.6 mass% to 2.5 mass% Ni, 0.1 mass% to 0.7 mass% Mg, and 0.2 mass%. The Si content is 0.7% by mass or less and the balance is Al and inevitable impurities.

  According to the aspect of the present invention, there is provided an aluminum alloy for conductive wires in which the temperature range of the solid-liquid coexistence region is widened and casting defects are suppressed.

  As one embodiment of the present invention, 0.1% by mass to 0.4% by mass Cu, 0.01% by mass to 0.05% by mass Ti, 0.001% by mass to 0.01% by mass One or more elements selected from the group consisting of the following B and B may be contained. Thereby, the aluminum alloy for conductive wires with which mechanical strength increases is provided.

  According to the aspect of the present invention, there is provided an aluminum alloy for conductive wires in which the temperature range of the solid-liquid coexistence region is widened and casting defects are suppressed.

  As another aspect of the present invention, the conductive wire has an alloy composition of 0.6 mass% to 2.5 mass% Ni, 0.1 mass% to 0.7 mass%, 2 mass% or more and 0.7 mass% or less of Si, the remainder consists of Al and inevitable impurities.

  As a desirable aspect, the alloy composition is 0.1 mass% or more and 0.4 mass% or less of Cu, 0.01 mass% or more and 0.05 mass% or less of Ti, and 0.001 mass% or more and 0.01 mass% or less. One or more elements selected from the group consisting of B and less than mass% may be included.

  As another aspect of the present invention, a method for manufacturing a wire harness includes 0.6 mass% to 2.5 mass% Ni, 0.1 mass% to 0.7 mass% Mg, and 0.2 mass%. Form an aluminum alloy stranded wire composed of Si and 0.7% by mass of Si and the balance consisting of Al and inevitable impurities, and insulate the surface of the stranded wire after solution treatment and aging treatment. After covering the resin and cutting the coated stranded wire to a predetermined length, terminals are provided at both ends of the cut stranded wire.

  According to the aspect which concerns on this invention, the manufacturing method of the aluminum alloy for conductive wires in which a casting defect is suppressed, a conductive wire, and a wire harness can be provided.

FIG. 1 is a diagram illustrating an example of an equilibrium diagram of an aluminum alloy according to the present embodiment. FIG. 2 is a diagram illustrating an example of an equilibrium diagram of an aluminum alloy according to the present embodiment. FIG. 3 is a diagram illustrating an example of an equilibrium diagram of an aluminum alloy according to the present embodiment. FIG. 4 is a diagram illustrating an example of an equilibrium diagram of an aluminum alloy according to a comparative example. FIG. 5 is an explanatory view schematically illustrating the entire structure of a belt-and-wheel casting machine that is a part of the casting machine of the Properti continuous casting and rolling machine. FIG. 6 is a partial cross-sectional view illustrating the structure of the circumferential groove.

  Hereinafter, embodiments according to the present invention will be described with reference to the drawings, but the present invention is not limited thereto. The components of the embodiments described below can be combined as appropriate. Some components may not be used. In addition, constituent elements in the embodiments described below include those that can be easily assumed by those skilled in the art, those that are substantially the same, and those in a so-called equivalent range.

[Wire Harness]
2. Description of the Related Art Wire harnesses in which terminals (connectors) are attached to conductive wires for passing current or electric signals are used in industrial equipment such as automobiles, trains, vehicles, airplanes, and robots. Copper (Cu) having good conductivity has been often used for the conductive wire of the wire harness. On the other hand, if the content ratio of aluminum (Al) contained in the conductive wire of the wire harness is increased, Al is less likely to affect the properties of the iron alloy than Cu, so Fe recycling (separation during disassembly) Improves. As a result, when industrial equipment is disassembled, costs can be reduced. Moreover, since Al has a smaller specific gravity than Cu, the wire harness becomes lighter, and the transportation cost of vehicles, airplanes and the like can be reduced. When the content ratio of Al contained in the conductive wire of the wire harness is increased, Cu resource depletion can be suppressed.

  Unlike electric wires for power transmission, wire harnesses are often wired so as to sew a limited space. Therefore, the handling of wires (ease of wiring) is important. Moreover, since the wire harness used for the door part etc. of a vehicle bends whenever a door is opened and closed, bending resistance is also requested | required. In the wire harness, when the conductive wire having a diameter of 1 mm or less is a twisted wire, handling of the conductive wire is facilitated. Moreover, in the wire harness, when the conductive wire having a diameter of 1 mm or less is a twisted wire, the bending resistance of the conductive wire is increased. And since a surface area can be increased more than one line | wire which has the same cross-sectional area because a wire harness is a strand wire, electrical conductivity becomes high.

[Aluminum alloy for conductive wire]
The aluminum alloy for conductive wires of the present embodiment includes 0.6 mass% or more and 2.5 mass% or less nickel (Ni), 0.1 mass% or more and 0.7 mass% or less magnesium (Mg), 0 .2 mass% or more and 0.7 mass% or less of silicon (Si), with the balance being Al and inevitable impurities.

In the Al alloy, Ni is not so solidly dissolved in the Al matrix, and forms a Ni—Al-based crystallized product (Ni ₃ Al or the like), contributing to an improvement in the mechanical strength of the conductive wire. When the mechanical strength is improved, the conductive wire is less likely to be disconnected when performing wire drawing or twisting. Ni has a small effect of increasing electrical resistance when added to an Al alloy, and further, since it does not dissolve so much in the Al matrix, there is little decrease in conductivity.

  1 to 3 are examples of an equilibrium diagram of an aluminum alloy according to the present embodiment. FIG. 4 is an example of an equilibrium diagram of an aluminum alloy according to a comparative example. The aluminum alloy shown in FIG. 1 contains 0.7% by mass of Ni and the balance is Al. The aluminum alloy shown in FIG. 2 contains 1.0% by mass of Ni and the balance is Al. The aluminum alloy shown in FIG. 3 contains 1.5% by mass of Ni and the balance is Al. The aluminum alloy shown in FIG. 4 contains 1.5% by mass of iron (Fe), and the balance is Al.

  For example, in the aluminum alloy shown in FIG. 4, the solid-liquid coexistence region (temperature range between the liquidus and solidus) is 654 ° C. or higher and 655 ° C. or lower. On the other hand, the aluminum alloy shown in FIG. 1 has a solid-liquid coexistence region of 640 ° C. or higher and 658 ° C. or lower when 0.7 mass% of Ni is included. Thus, when the aluminum alloy of this embodiment contains 0.7 mass% or more of Ni, the solid-liquid coexistence region becomes larger than the comparative example.

  The aluminum alloy shown in FIG. 2 contains 1.0% by mass of Ni, and the solid-liquid coexistence region is 640 ° C. or higher and 657 ° C. or lower. The aluminum alloy shown in FIG. 3 contains 1.5% by mass of Ni, and the solid-liquid coexistence region is 640 ° C. or higher and 656 ° C. or lower. Thus, if the aluminum alloy of this embodiment contains 0.7 mass% or more and 1.5 mass% or less of Ni, the solid-liquid coexistence region becomes 16 ° C. or more and 18 ° C. or less, and the content of Ni is reduced. In contrast, the change in the solid-liquid coexistence region is small. As for the liquidus temperature, pure Al is the highest, and when the Ni content approaches 5.5% by mass, which is a standard for phase transformation to the eutectic composition of the Al—Ni alloy, the liquidus temperature gradually decreases. Conversely, when the Ni content exceeds 5.5% by mass, the liquidus temperature tends to increase. In the case of the aluminum alloy composition for conductive wires of this embodiment, since Ni is a hypoeutectic composition range less than the eutectic composition, the liquidus temperature tends to decrease as the Ni content increases.

  In the aluminum alloy of this embodiment, since the solid-liquid coexistence region is larger than that of the aluminum alloy of the comparative example, the management of the casting temperature during casting is facilitated, and casting defects are suppressed. As a result, the castability of the aluminum alloy of this embodiment is improved as compared with the aluminum alloy of the comparative example.

  In the aluminum alloy of the present embodiment, when Ni is contained in an amount exceeding 2.5% by mass, a coarse Ni—Al-based crystallized substance that may become a starting point of breakage at the time of wire drawing is easily formed. Become. For this reason, in the aluminum alloy of this embodiment, the fracture | rupture at the time of a wire drawing process is suppressed because Ni is 2.5 mass% or less. The aluminum alloy of the present embodiment is more preferable because Ni is 2.0% by mass or less because coarse Ni—Al-based crystallized substances are reduced and breakage during wire drawing is further suppressed. . When Ni is 2.5% by mass or less, since the amount of Ni dissolved in the Al matrix is small, the decrease in conductivity is small even when compared with the conductivity of pure Al.

Mg and Si form an Mg—Si based precipitate (Mg ₂ Si or the like) while performing an aging treatment, and contribute to improvement of mechanical strength. When the mechanical strength is improved, the conductive wire is less likely to be disconnected when performing wire drawing or twisting. In the aluminum alloy for conductive wires of this embodiment, 0.1 mass% or more of Mg is contained, and if 0.2 mass% or more of Si is contained, the effect of increasing the mechanical strength becomes remarkable. In the aluminum alloy for conductive wires of the present embodiment, when Mg exceeding 0.7% by mass is contained, a coarse Mg-Si crystallized product that may become a starting point of breakage during wire drawing is obtained. It becomes easy to do. In the aluminum alloy for conductive wires of the present embodiment, the amount of Mg contained is 0.7% by mass or less, so that the solid solution amount of Mg in the Al matrix is reduced and the decrease in conductivity is suppressed. it can. In the aluminum alloy for conductive wires of this embodiment, when Si exceeding 0.7 mass% is contained, a coarse Mg-Si based crystallized substance that may become a starting point of breakage during wire drawing is obtained. It becomes easy to do. In the aluminum alloy for conductive wires of the present embodiment, the amount of Mg contained is 0.7% by mass or less, so that the solid solution amount of Mg in the Al matrix is reduced and the decrease in conductivity is suppressed. it can.

The aluminum alloy for conductive wires of this embodiment may further contain Cu. Cu has an effect of improving mechanical strength, and when further subjected to aging treatment, forms Al—Cu-based precipitates (Al ₂ Cu, etc.), and further contributes to improvement of mechanical strength. In the aluminum alloy for conductive wires of this embodiment, when 0.1 mass% or more of Cu is contained, the effect of increasing the mechanical strength becomes remarkable. In the aluminum alloy for conductive wires of this embodiment, when Cu exceeding 0.4 mass% is contained, the deformation resistance is increased, and the drawability of the conductive wires may be reduced.

  The aluminum alloy for conductive wires of this embodiment may further contain at least one of titanium (Ti) and boron (B). Ti or B has an effect of contributing to refinement of the cast structure, and has an effect of improving castability and workability. When the aluminum alloy for conductive wires of this embodiment contains 0.01 mass% or more of Ti or 0.001 mass% or more of B, the effect of refining the cast structure becomes remarkable. In the aluminum alloy for conductive wires of this embodiment, if the Ti content exceeds 0.05% by mass or the B content exceeds 0.01% by mass, the electrical conductivity will be significantly reduced.

  For example, the aluminum alloy for conductive wires of the present embodiment is substantially 0.6 mass% to 2.5 mass% Ni, 0.1 mass% to 0.7 mass% Mg, 0% .2% to 0.7% by mass of Si and the balance of Al. The aluminum alloy for conductive wires of this embodiment may contain inevitable impurities. The aluminum alloy for conductive wires of the present embodiment includes 0.6 mass% or more and 2.5 mass% or less of Ni, 0.1 mass% or more and 0.7 mass% or less of Mg, and 0.2 mass% or more of 0. .7% by mass or less of Si, the balance of Al and inevitable impurities.

  Inevitable impurities are not intentionally added, but are substances that may be inevitably mixed in the raw material or in the manufacturing process. Inevitable impurities include Fe and vanadium (V), manganese (Mn), chromium (Cr), zirconium (Zr) and the like.

  When Fe is contained in an Al alloy, it has an effect of improving the mechanical strength of the Al alloy, but when the Fe content is large, the electrical conductivity is lowered. Fe forms an Al-Fe-Si-based crystallized product and suppresses the precipitation of Mg-Si-based precipitates that contribute to the improvement of strength. Therefore, in the aluminum alloy of this embodiment, even if Fe is contained. Although it is good, it is set as 0.4 mass% or less content. In the aluminum alloy of the present embodiment, Fe may be contained, but the conductivity can be improved by using Fe of less than 0.1% by mass.

  V has a particularly large effect on conductivity. When the amount of V exceeds 0.002% by mass in the aluminum alloy for conductive wires of this embodiment, the decrease in conductivity becomes large. In the aluminum alloy of this embodiment, V may be contained, but the conductivity can be improved by setting V to 0.002 mass% or less. The inevitable impurities include other elements, but if the content of the other elements is increased, the conductivity is lowered. Therefore, it is preferable to control the content to less than 0.1% by mass, preferably 0.05% by mass or less. .

[Production method]
Below, an example of the process of manufacturing a wire harness is demonstrated using the aluminum alloy of the embodiment mentioned above.

(Dissolution process)
JIS H2110 standard aluminum ingot is melted as a molten aluminum alloy after the mother alloy of the additive element is added. However, when Ti and B are added as a refining material, the master alloy of Ti and B is added to the molten aluminum alloy immediately before casting.

(Casting process)
The obtained aluminum alloy molten metal is subjected to molten metal processing such as component adjustment, removal, and degassing. When Ti and B are added as a refined material, a rod hardener (a refined material) formed of an Al-Ti-B alloy is added to the molten aluminum alloy before casting. The continuous casting and rolling machine pours a molten aluminum alloy into a mold portion, casts the aluminum alloy of the embodiment, performs continuous rolling, and casts and rolls into a rough drawing line shape of φ9.5 mm.

  Hereinafter, casting and rolling will be described in detail with reference to FIGS. 5 and 6. FIG. 5 is an explanatory view schematically illustrating the entire structure of a belt-and-wheel casting machine that is a part of the casting machine of the Properti continuous casting and rolling machine. As shown in FIG. 5, a belt and wheel casting machine, a rotary casting wheel 1, a circumferential groove 2, an endless belt 3, a spout 4 and a roll 5 are provided. A circumferential groove 2 is formed on the circumferential surface of the rotary casting wheel 1, and an endless belt is brought into contact with the circumferential surface of the rotary casting wheel 1 so as to cover the circumferential groove 2 over an angle range of about 200 degrees. 3 runs. In addition, the said angle range is suitably changed with an apparatus.

  FIG. 6 is a partial cross-sectional view illustrating the structure of the circumferential groove. As shown in FIG. 6, the endless belt 3 is pressed against the outer peripheral surface of the rotary casting wheel 1 by the roll 5, and the inside of the circumferential groove 2 covered with the endless belt 3 becomes a casting cavity.

  A molten aluminum alloy having a composition described later is continuously supplied into the casting cavity by the spout 4. The supplied molten metal is cooled and solidified by the rotary casting wheel 1 and the endless belt 3 with the assistance of cooling water not shown. If the temperature of the molten aluminum alloy supplied to the casting cavity is too high, it will not solidify well, resulting in casting failure and casting defects. Conversely, if the temperature of the molten aluminum alloy supplied to the casting cavity is too low, it will solidify during the supply to the casting cavity, which will also cause casting failure and casting defects. For this reason, it is important to control the temperature at which the molten aluminum alloy is supplied to the casting cavity. However, in the case of the aluminum alloy for conductive wires of this embodiment, the temperature range of solid-liquid coexistence is relatively wide. The temperature control of the molten metal becomes easy.

  When the endless belt 3 is detached from the circumferential groove 2 as the rotary casting wheel 1 rotates, the cast body 6 is also detached from the circumferential groove 2. When the tip portion of the cast body 6 is bent slightly (about 10 to 20 degrees) when it is completely separated from the circumferential groove 2, the cast body 6 continues without contacting the endless belt 3 again as casting proceeds. It is taken out from the casting machine. The cast body 6 produced in this way has a small amount of oxides or the like during casting and does not have a free solidified surface that is solidified by contact with air, so that a product with very little oxide as a whole can be obtained. Sent to the rolling process.

  The cast body 6 taken out from the continuous casting machine is guided to a rolling mill (not shown). Since the cast body 6 taken out from the rotary casting wheel 1 is solidified and bent along the curved surface of the circumferential groove 2, the cast body is straightened through a roll straightening machine before being guided to the rolling mill. Is preferred.

  Since the cast body 6 guided to the rolling mill is still maintained at a considerably high temperature, it is usually hot-rolled as it is to produce a rough drawn wire. If the temperature at the entrance of the rolling mill is too low, a heating device can be installed in front of the rolling mill to adjust the temperature to rise. It is preferable in terms of cost to control the temperature at the outlet.

  During rolling, a lubricant emulsion that also serves as cooling may be used. If the reduction rate of the cross section during rolling is small, the cast hole in the ingot cannot be sufficiently crushed, and cracks are likely to occur during winding of the rough drawn wire or after drawing of the rough drawn wire. . Moreover, when the cross-section reduction rate is large, the temperature drop of the ingot during rolling becomes severe, and the rough drawn wire becomes difficult to roll. For this reason, it is preferable to perform rolling in the range of a cross-sectional reduction rate of 60% or more and 98% or less.

  In addition, without using a continuous casting machine and a rolling mill, after a molten aluminum alloy was cast into a cylindrical ingot (billet) by DC casting, it was formed into a solid round bar of φ9.5 mm by extrusion. Also good.

(Wire drawing process)
The rough drawing wire obtained by the casting process described above is drawn so as to have a predetermined wire diameter. In the wire drawing process, if an annealing process at a predetermined temperature is interposed as required, the wire drawing process is facilitated. In addition, an annealing process is performed before a wire drawing process, the middle of a wire drawing process, and after completion | finish of a wire drawing process as needed. After rolling, after winding the rough wire once, annealing and cold wire drawing may be performed again. The annealing treatment may be performed by batch processing or continuous annealing by energization.

(Twisting process)
A twisting process of twisting a plurality of drawn wires obtained by the drawing process is performed. Next, compression processing is performed so that the obtained stranded wire has a predetermined cross-sectional area.

(Solution treatment process)
After the twisted wire obtained by the twisting process is subjected to a solution treatment, water quenching is performed.

  By the solution treatment of the stranded wire, the Mg-Si compound or Al-Cu compound crystallized during casting is dissolved in the matrix, and Mg, Si and Cu in the matrix are dissolved. The amount of solid solution increases.

  And, when the stranded wire is quenched by water quenching, it is suppressed that one or more elements selected from Mg, Si and Cu are precipitated during cooling, and one kind selected from Mg, Si and Cu. The state where the solid solution amount of the above elements is high is maintained.

  In addition, as solution treatment conditions, it is preferable to hold | maintain the solution treatment temperature of 520 degreeC or more and 560 degrees C or less for 0.5 hours (hr) or more and 12 hours (hr) or less. When the solution treatment temperature is less than 520 ° C. or the temperature holding time is less than 0.5 hours (hr), the effect of solution treatment is small. When the solution treatment temperature is higher than 560 ° C., local melting may occur. Further, even if the temperature holding time exceeds 12 hours (hr), the change in the solid solution amount of one or more elements selected from Mg, Si and Cu is not observed, resulting in an increase in cost.

(Aging process)
In the solution treatment step, an aging treatment is performed on the solution-treated strands. By performing the aging treatment, a fine Mg-Si compound or Al-Cu compound that contributes to improving strength is precipitated, the strength is improved, and the solid solution amount of Mg, Si, and Cu in the matrix phase is increased. The electrical conductivity is also improved. As preferable aging conditions, the aging treatment temperature is 150 ° C. or more and 200 ° C. or less, and the temperature holding time is 0.5 hours (hr) or more and 14 hours (hr) or less. If the aging treatment temperature is less than 150 ° C. or the temperature holding time is less than 0.5 hour (hr), precipitation is not sufficient. On the other hand, if the aging treatment temperature exceeds 200 ° C. or the temperature holding time exceeds 14 hours (hr), the precipitates may become coarse and the wire drawing property may be reduced.

(Coating)
The stranded wire subjected to the aging treatment is coated with an insulating resin. After covering with the insulating resin, the stranded wire is cut into a predetermined length. Terminals are provided at both ends of the stranded wire, and a wire harness is manufactured.

[Example]
Next, examples according to the present invention will be described. A molten aluminum alloy having the composition shown in Table 1 was prepared and subjected to molten metal treatment such as degassing and degassing. After the molten metal treatment, it was filtered with a CFF (ceramic foam filter), and a rough drawing line of φ9.5 mm was obtained by a continuous casting and rolling method.

  The obtained rough drawing wire is drawn to φ3.2 mm, and then annealed at an annealing temperature of 300 ° C. and 10 hours (hr). Next, the obtained rough drawing wire was drawn to φ1.0 mm. The obtained conductive wire is subjected to a solution treatment step at a solution treatment temperature of 540 ° C. and a holding time of 10 hours (hr), and is cooled with water. After the solution treatment step, an aging treatment step with an aging treatment temperature of 180 ° C. and a holding time of 10 hours (hr) was processed to obtain a conductive wire sample of φ1.0 mm.

  As shown in Table 1, with respect to 20 types of conductive aluminum alloys having different compositions, samples of conductive wires of φ1.0 mm (Samples 1 to 12 as examples of the present invention, Samples 13 to 20 as comparative examples) Were prepared and the performance of each of these samples was evaluated. The composition of each material can be analyzed by analyzing a sample obtained by solidifying a molten aluminum alloy collected immediately before the rotary casting wheel 1 by an emission analysis method based on the JIS H1305 standard.

  As the first performance evaluation, a tensile test was performed based on the JIS Z 2241 (1998) test, and the tensile strength (Ultimate Tensile Strength, UTS) and elongation were measured. The results of tensile strength and elongation are shown in Table 1.

  As for the tensile strength, the tensile strength was evaluated, a sample having a tensile strength exceeding 150 [MPa] was evaluated as “Y”, and a sample having a tensile strength of 150 [MPa] or less was evaluated as “N”. The tensile strength results are shown in Table 1.

  Further, as the second performance evaluation, the conductivity was measured by the test method of JIS H0505, and the results of the conductivity are also shown in Table 1. A sample having an electric conductivity of 50 [% IACS] or higher was evaluated as “Y”, and a sample having an electric conductivity of less than 50 [% IACS] was evaluated as “N”.

  In addition, as a third performance evaluation, when drawing from φ3.2 mm to φ1.0 mm, the drawability was also confirmed, and when an 8,000 kg φ3.2 mm wire was drawn to φ1.0 mm, the wire was broken. A sample in which the occurrence occurred was evaluated as “N”, and a sample in which the occurrence did not occur was evaluated as “Y”.

  Examples 1 to 12 correspond to the aluminum alloy for conductive wires according to the above-described embodiment.

  The aluminum alloy for conductive wire of Comparative Example 13 has less Ni, Si, Mg content than the aluminum alloy for conductive wire of Examples 1 to 12 of the present invention, and the evaluation of tensile strength is “N”. There is a problem.

Since the aluminum alloy for conductive wires of Comparative Example 14 has a lower Si content than the aluminum alloys for conductive wires 1 to 12 which are the examples of the present invention, Mg-Si based precipitates (Mg ₂ Si, etc.) There is a problem that evaluation of tensile strength is “N”. There is a problem that the Mg content is large with respect to the Si content, the Mg solid solution amount is large with respect to the Al matrix, and the conductivity is evaluated as “N”.

The aluminum alloy for conductive wires of Comparative Example 15 has a lower Mg content than the aluminum alloys for conductive wires of 1 to 12 which are the examples of the present invention. Therefore, Mg-Si based precipitates (Mg ₂ Si, etc.) There is a problem that evaluation of tensile strength is “N”.

  Since the aluminum alloy for conductive wires of Comparative Example 16 has a higher Mg content than the aluminum alloys for conductive wires 1 to 12 which are the examples of the present invention, the Mg content relative to the Si content However, there is a problem that the solid solution amount of Mg increases with respect to the Al matrix and the conductivity is evaluated as “N”. The wire drawing evaluation is “N” because Mg containing more than 0.7% by mass contains coarse Mg—Si-based crystallization that may be the starting point of fracture during wire drawing. This is thought to be because it becomes easier to make things.

  The aluminum alloy for conductive wires of Comparative Example 17 has a higher Si content than the aluminum alloys for conductive wires 1 to 12 which are the examples of the present invention. For this reason, the evaluation of the drawability is “N” because it contains more than 0.7% by mass of Si, which is a coarse Mg—Si that may be the starting point of fracture during wire drawing. This is thought to be because it becomes easier to form a system crystallized product.

  The aluminum alloy for conductive wires of Comparative Example 18 has a higher Ni content than the aluminum alloy for conductive wires of 1 to 12, which is an example of the present invention, and Ni is contained in excess of 2.5% by mass. . The reason why the wire drawing property is evaluated as “N” is considered to be that a coarse Ni—Al-based crystallized substance that may become a starting point of breakage at the time of wire drawing is easily formed.

  The aluminum alloy for conductive wires of Comparative Example 19 has a higher Cu content than the aluminum alloy for conductive wires of 1 to 12, which is an example of the present invention, and Cu is contained in excess of 0.4% by mass. . The evaluation of the drawability is “N” because the deformation resistance is increased and the drawability of the conductive wire is lowered. Moreover, the aluminum alloy for conductive wires of Comparative Example 19 has a problem that the Cu content is large, the solid solution amount of Cu is large with respect to the Al matrix, and the conductivity evaluation is “N”.

  The aluminum alloy for conductive wires of Comparative Example 20 contains more Fe than the aluminum alloy for conductive wires 1 to 12 which is an example of the present invention, and Fe is contained in excess of 0.4 mass%. . It is considered that the evaluation of the tensile strength is “N” in order to suppress the precipitation of Mg—Si based precipitates that form Al—Fe—Si based crystals and contribute to the improvement of strength. .

  As described above, the aluminum alloy for conductive wires of Examples 1 to 12 of the present invention includes 0.6 mass% to 2.5 mass% nickel (Ni) and 0.1 mass% to 0 mass%. 0.7% by mass or less of magnesium (Mg), 0.2% by mass or more and 0.7% by mass or less of silicon (Si), and the balance is made of Al and inevitable impurities. Thereby, the aluminum alloy for conductive wires of Example 1 to Example 12 is excellent in mechanical strength, wire drawability, and electrical conductivity. Furthermore, the total content of Ni, Mg, and Si is preferably 1.1% by mass or more. When the total content of Ni, Mg, and Si is 1.1% by mass or more, the mechanical strength characteristics can be improved.

  And the conductive wire formed with the aluminum alloy for conductive wires of Examples 1 to 12 of the present invention also has improved bending resistance. When the conductive wire formed of the aluminum alloy for conductive wires of 1 to 12, which is an embodiment of the present invention, is a stranded wire of φ1 mm or less and twisted, when used for a wire harness, the conductive wire is routed. Becomes easy. Moreover, in the wire harness, when the conductive wire having a diameter of 1 mm or less is a twisted wire, the bending resistance of the conductive wire is increased. And since a surface area can be increased more than one line | wire which has the same cross-sectional area because a wire harness is a strand wire, electrical conductivity becomes high.

  The temperature range of the solid-liquid coexistence region is wider than the aluminum alloy of Patent Document 1 described above, and the aluminum alloy for conductive wires 1 to 12 which is an example of the present invention makes it easy to manage the casting temperature during casting, Casting defects are suppressed.

  In the above, various useful examples of the present invention have been shown and described. The present invention is not limited to the various embodiments and modifications described above, and various modifications can be made without departing from the gist of the present invention and the contents described in the appended claims. There is no.

1 Rotating casting wheel 2 Circumferential groove 3 Endless belt 4 Spout 5 Roll 6 Casting body

Claims (3)

  The alloy composition is 0.6 mass% to 2.5 mass% Ni, 0.1 mass% to 0.7 mass% Mg, and 0.2 mass% to 0.7 mass% Si. And the wire harness which has a conductive wire which the remainder consists of Al and an unavoidable impurity. The alloy composition is
0.1 mass% or more and 0.4 mass% or less of Cu;
0.01 mass% or more and 0.05 mass% or less of Ti,
0.001 mass% or more and 0.01 mass% or less B,
The wire harness according to claim 1, comprising at least one element selected from the group consisting of: 0.6 mass% or more and 2.5 mass% or less of Ni, 0.1 mass% or more and 0.7 mass% or less of Mg, 0.2 mass% or more of 0.7 mass% or less of Si, and the balance Forming a stranded wire of aluminum alloy consisting of Al and inevitable impurities,
After solution treatment and aging treatment for the stranded wire,
Covering the surface of the stranded wire with an insulating resin,
A method of manufacturing a wire harness, comprising: cutting the stranded wire after coating into a predetermined length; and providing terminals at both ends of the cut stranded wire.

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