EP2868757B1 - Fil en alliage de cuivre, et procédé de fabrication de celui-ci - Google Patents

Fil en alliage de cuivre, et procédé de fabrication de celui-ci Download PDF

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EP2868757B1
EP2868757B1 EP13812970.5A EP13812970A EP2868757B1 EP 2868757 B1 EP2868757 B1 EP 2868757B1 EP 13812970 A EP13812970 A EP 13812970A EP 2868757 B1 EP2868757 B1 EP 2868757B1
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Prior art keywords
wire
heating
copper alloy
mass
working
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German (de)
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EP2868757A1 (fr
EP2868757A4 (fr
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Tsukasa Takazawa
Satoshi Teshigawara
Toshio Abe
Shuji Tomimatsu
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Furukawa Electric Co Ltd
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Furukawa Electric Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • 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
    • C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon
    • 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
    • H01B1/026—Alloys based on copper

Definitions

  • the present invention relates to a copper alloy wire and a method of producing the same, and more specifically the present invention relates to an extra-fine copper alloy wire for magnet wires and a method of producing the same.
  • a coil for micro speakers that is used in mobile phones, smart phones, and the like, is produced by working an extra-fine wire (a magnet wire) having a wire diameter of 0.1 mm or less by winding into a coil shape.
  • Patent Literature 1 proposes a technique of using a high-concentration Cu-Ag alloy containing 2 to 15 mass% of Ag that can enhance the tensile strength almost without lowering the electrical conductivity.
  • Patent Literature 1 proposes a technique of using a high-concentration Cu-Ag alloy containing 2 to 15 mass% of Ag that can enhance the tensile strength almost without lowering the electrical conductivity.
  • Patent Literature 1 proposes a technique of using a high-concentration Cu-Ag alloy containing 2 to 15 mass% of Ag that can enhance the tensile strength almost without lowering the electrical conductivity.
  • Patent Literature 1 proposes a technique of using a high-concentration Cu-Ag alloy containing 2 to 15 mass% of Ag that can enhance the tensile strength almost without lowering the electrical conductivity.
  • Patent Literature 2 there is a proposal of a technique of achieving a balance between physical strength and elongation even in a low-concentration alloy, by carrying out the heating at a temperature lower than or equal to the softening temperature (Patent Literature 2).
  • this method is difficult to control the heating temperature and time period.
  • Patent Literature 3 there is a proposal of a technique of performing a semi-softening treatment of achieving a balance between physical strength and elongation, by adding 0.05 to 0.2 mass% of Ag and 0.003 to 0.01 mass% of Zr into copper to widen the softening temperature range.
  • US 2002/0066503 A1 discloses an ultrafine copper alloy wire with a diameter of not more than 0.08 mm, consisting of Cu, Ag and, optionally, Mg, In or Sn.
  • JP 2005 089805 A discloses an ultrafine copper alloy wire with a diameter of less than 0.2 mm, consisting of 1-10% Ag, 0.01-0.5% Mg and Cu as balance; and a manufacturing method.
  • Patent Literature 3 the method of performing a semi-softening treatment by adding a trace amount of Zr to a low-concentration Cu-Ag alloy (Patent Literature 3) can easily achieve a balance between elongation and physical strength; however, the method is insufficient in view of strength enhancement.
  • the shape of magnet wires is not limited to round wires, and investigations have also been conducted on the employment of square wires and rectangular wires. Even in the cases of these square wires and rectangular wires, it is requested to employ a wire with a thickness that is thin to the extent of that corresponding to the wire diameter of the round wire.
  • the present invention was achieved in view of the problems in those conventional art, and it is an object of the present invention to provide, at low cost, a copper alloy wire that is excellent in physical strength, elongation, and electrical conductivity, and that is suitable for the use in, for example, magnet wires.
  • the inventors of the present invention conducted thorough investigations on various copper alloys and heating conditions therefor, in order to develop a copper alloy wire that is superior in physical strength, elongation, and electrical conductivity than conventional alloy wires, and that is suitably used in magnet wires, and the like. As a result, the inventors have found that, when a Cu-Ag-Mg alloy wire is subjected to a semi-softening treatment, the resultant alloy wire is highly excellent in elongation and physical strength, and realization of characteristics by heating can be achieved readily.
  • the inventors have found that, when Ag and Mg are added to Cu each at a predetermined content and this alloy is subjected to a semi-softening treatment, it is possible to obtained, at low cost, a copper alloy wire that is excellent in physical strength, electrical conductivity, and elongation, and that is suitable for the use in, for example, magnet wires.
  • the present invention was completed based on those findings.
  • the present invention provides the following means:
  • a semi-softened state means a state in which elongation of the copper alloy wire satisfies 7% to 30%.
  • a semi-softening treatment means a heating that brings about the semi-softened state.
  • the semi-softening temperature range means a range of heating temperature that brings about a state in which elongation of the copper alloy wire after heating satisfies 7% to 30%.
  • a softening temperature means a heating temperature that brings about a state in which, in a copper alloy wire after heating, the tensile strength is no longer lowered. Referring to Fig.
  • the heating temperature at which the gradient of a drop curve of tensile strength becomes 0 (zero) is the softening temperature.
  • the heating temperature range means the temperature range in which a desired physical strength is retained after heating, and within the semi-softening temperature range. However, if the copper alloy wire is subjected to heating at a high temperature exceeding this softening temperature (a temperature on the righter side with respect to the softening temperature in Fig. 3 ), tensile strength is slightly further lowered due to overheating.
  • a softened state means a recovered state in which elongation of a copper alloy wire is more than 30%. Furthermore, a softening treatment means a heating at a high temperature that brings about the softened state.
  • a wire means to include a square wire or a rectangular wire, in addition to a round wire.
  • the wire of the present invention collectively means a round wire, a square wire, and a rectangular wire.
  • the size of the wire means, in the case of a round wire (the cross-section in the transverse direction (TD) is circular), the wire diameter ⁇ (the diameter of the circle of the cross-section) of the round wire; in the case of a square wire (the cross-section in the transverse direction is square), the thickness t and the width w (each being the length of one side of the square of the cross-section and being identical to each other) of the square wire; and in the case of a rectangular wire (the cross-section in the transverse direction is rectangular), the thickness t (the length of a shorter side of the rectangle of the cross-section) and the width w (the length of a longer side of the rectangle of the cross-section) of the rectangular wire.
  • the alloy wire of the present invention is excellent in tensile strength, elongation, and electrical conductivity
  • the alloy wire is preferably suitable as, for example, a copper alloy wire for magnet wires.
  • the Cu-Ag-Mg alloy wire of the present invention can exhibit performance with a smaller amount of the Ag content as compared with conventional Cu-Ag alloy wires having large Ag contents, the wire can be produced at a lower cost.
  • the method of producing a Cu-Ag-Mg alloy wire of the present invention since the temperature range for carrying out a semi-softening heating is wide, a stable Cu-Ag-Mg alloy wire can be produced, which is excellent in the performance, and which has less fluctuation in the performance.
  • the copper alloy wire of the present invention contains 0.5 mass% to 4.0 mass% of Ag, and 0.05 mass% to 0.5 mass% of Mg, with the balance being Cu and unavoidable impurities.
  • the physical strength can be enhanced almost without lowering the electrical conductivity. Furthermore, it can be made easier to carry out a semi-softening heating, by enhancing heat resistance.
  • the Ag content is set to 0.5 to 4.0 mass%, and more preferably 0.5 to 2.0 mass%. If the content of Ag is too small, sufficient physical strength cannot be obtained. Also, if the Ag content is too large, electrical conductivity is lowered, and also it becomes excessively high cost. Moreover, the heating temperature becomes so high that heating cannot be carried out easily.
  • an extra-fine magnet wire can be obtained, which has an enhanced tensile strength upon semi-softening and which is excellent in physical strength. Furthermore, the semi-softening temperature range is widened, and thereby that the heating temperature range is widened for obtaining the characteristics required for extra-fine magnet wires (a tensile strength of 350 MPa or more, and an elongation of 7% or more), to allow stable production.
  • the Mg content is set to 0.05 to 0.5 mass%, and more preferably 0.05 to 0.3 mass%. If the Mg content is too small, the effects become insufficient for: enhancing the physical strength upon semi-softening; and extending the semi-softening temperature range. Furthermore, if the Mg content is too large, electrical conductivity is conspicuously lowered.
  • the copper alloy wire of the present invention may have an alloy composition containing Ag at a content of 0.5 mass% to 4.0 mass%, Mg at a content of 0.05 mass% to 0.5 mass% and at least one selected from the group consisting of Sn, Zn, In, Ni, Co, Zr, and Cr at a respective content of 0.05 to 0.3 mass%, with the balance being Cu and unavoidable impurities.
  • the at least one element selected from the group consisting of Sn, Zn, In, Ni, Co, Zr, and Cr is an optional alloying element in the copper alloy according to the present invention.
  • the contents of those elements are, respectively, 0.05 to 0.3%, and preferably 0.05 % to 0.2%. If this content is too small as the respective content, the effect of strength enhancement owing to the addition of any of these elements cannot be expected in most cases. Also, if this content is too large, since the lowering of the electrical conductivity is too large, the resultant copper alloy is inappropriate as a copper alloy wire, such as a magnet wire.
  • These elements each are a solid solution strengthening-type or precipitation strengthening-type element, and when any of these elements is/are added to Cu, physical strength can be enhanced without lowering the electrical conductivity to a large extent. As a result of this addition, the physical strength of the copper alloy wire itself is enhanced, and the resistance to bending fatigue is enhanced.
  • the tensile strength of the copper alloy wire of the present invention is set to 350 MPa or more, because, if the tensile strength is less than 350 MPa, the strength is insufficient when the diameter is made finer by wire-drawing, and the wire is poor in resistance to bending fatigue.
  • the elongation of the copper alloy wire of the present invention is set to 7% or more but 30% or less, because, if the elongation is less than 7%, the wire is poor in workability, and the resultant wire is occurred with defects, such as wire breakage, at the time of forming into a coil.
  • the shape of the copper alloy wire of the present invention is not limited to a round wire, and may also be a square wire or a rectangular wire. Then, these will be described below.
  • the method of producing a copper alloy round wire of the present invention is carried out by performing the steps, for example, of: casting; cold-working (cold-wire-drawing); intermediate heating (intermediate annealing); and final-heating (final-annealing), in this order.
  • the intermediate annealing may be omitted.
  • Raw materials of Cu, Ag, and Mg are melted and cast in a casting machine having the interior (internal walls) preferably made of carbon, for example, in a graphite crucible.
  • the atmosphere inside the casting machine at the time of melting is preferably selected to be a vacuum or an inert gas atmosphere, such as nitrogen or argon, in order to prevent occurrence of oxides.
  • an inert gas atmosphere such as nitrogen or argon
  • a roughly-drawn rod having a diameter of generally about ⁇ 8 to 23 mm is similarly obtained, by subjecting the billet (casting ingot) obtained by casting, to wire-drawing.
  • the roughly-drawn rod When this roughly-drawn rod is subjected to cold-working, the roughly-drawn rod is worked into a fine diameter wire having a diameter of ⁇ 0.1 mm or less. Regarding this cold-working, it is preferable to perform cold wire-drawing.
  • the working ratio in this cold-working may vary depending on the target wire diameter, the copper alloy composition, and the heating conditions, and there are no particular limitations.
  • the working ratio is generally set to 70.0 to 99.9%.
  • this cold-working includes a plurality of cold-working steps, such as first cold-working (wire-drawing) and second cold-working (wire-drawing), intermediate annealing (intermediate heating) may be carried out in the mid course of the first cold-working and the second cold-working.
  • first cold-working wire-drawing
  • second cold-working wire-drawing
  • intermediate annealing intermediate heating
  • the heating method of performing the intermediate annealing may be roughly classified into a batch-type method and a continuous method. Since the batch-type heating requires a longer treatment time period and a larger cost, this method is rather poor in productivity. However, since it is easy to perform the /control of temperature or retention time period, it is easy to perform the control of characteristics. On the contrary, since the continuous-type heating can carry out heating and the wire-drawing continuously, this is excellent in productivity. However, since it is necessary to perform this heating in a very short time period, it is necessary to precisely control the heating temperature and time period, to realize characteristics stably. Those heating methods have advantages and disadvantages as described above, and therefore, it is desirable to select the heating method according to the purpose.
  • the batch-type heating for example, it is preferable to perform heating in a heating furnace in an inert atmosphere, such as nitrogen or argon, at 300°C to 600°C for 30 minutes to 2 hours.
  • an inert atmosphere such as nitrogen or argon
  • Examples of the continuous-type heating include an electrically heating-type heating and an in-atmosphere running-type heating.
  • the electrically heating-type heating is a method of: providing electrode rings in the mid course of the wire-drawing step; passing an electric current to the copper alloy wire that passes among the electrode rings; and performing heating by the Joule heat generated by the copper alloy wire itself.
  • the in-atmosphere running-type heating is a method of: providing a vessel for heating in the mid course of wire-drawing; and performing heating by passing a copper alloy wire in the atmosphere of the vessel for heating that has been heated to a predetermined temperature (for example, 300°C to 600°C).
  • the copper alloy wire that has been worked to a desired size (wire diameter) by the steps described above, is subjected to finish-annealing as the final-heating.
  • Examples of the heating method of conducting finish-annealing include, similarly to the intermediate annealing, a batch-type heating and a continuous-type heating.
  • the tensile strength and elongation in the wire after the final-heating may undergo slight changes, depending on the composition of copper alloy wire or the working ratio.
  • the heating temperature and the heating retention time period for the finish-annealing are appropriately adjusted such that the elongation of the copper alloy wire obtainable by this final-heating would be 7 to 30%, preferably 10 to 20%.
  • the final-heating is carried out at a higher temperature when the heating time period is short, and is carried out at a lower temperature when the heating time period is long.
  • the heating time period since the heating time period is short, it is preferable to perform the heating for 0.1 to 5 seconds at 300°C to 700°C.
  • a longer heating time period can be employed, and it is preferable to perform the heating for 30 to 120 minutes at 300°C to 600°C.
  • the method of producing a copper alloy rectangular wire of the present invention is the same as the method of producing a round wire described above, except for containing rectangular wire-working.
  • the method of producing a rectangular wire of the present invention is carried out by performing the steps, for example, of: casting; cold-working (cold wire-drawing); rectangular wire-working; and final-heating (final-annealing), in this order.
  • the intermediate annealing intermediate heating
  • the conditions of the steps of working and heating such as casting, cold-working, intermediate annealing, and final-annealing, as well as the preferred conditions thereof, are also the same as those for the method of producing a round wire.
  • the production process is the same as that for the round wire, in which an ingot obtained by casting is subjected to cold-working (wire-drawing) to obtain a roughly-drawn rod having a round wire shape, and the roughly-drawn rod is further subjected to intermediate annealing if necessary.
  • the round wire (roughly-drawn rod) thus obtained is subjected to cold rolling using a rolling machine, cold rolling using a cassette roller die, pressing, drawing, and the like.
  • the transverse direction (TD) cross-section shape is worked into a rectangular shape, to obtain the shape of a rectangular wire. This rolling and the like are generally carried out in one to five passes.
  • the reduction ratio in each pass and the total reduction ratio at the time of rolling and the like are not particularly limited, and may be appropriately set to obtain a desired rectangular wire size.
  • the reduction ratio is the ratio of change in the thickness in the rolling direction upon performing the rectangular wire-working, and when the thickness before rolling is designated as t 1 , and the thickness of the wire after rolling is designated as t 2 , the reduction ratio (%) is represented by: ⁇ 1 - (t 2 /t 1 ) ⁇ ⁇ 100.
  • this total reduction ratio can be adjusted to 10 to 90%, and the reduction ratio in each pass can be adjusted to 10 to 50%.
  • the aspect ratio is generally 1 to 50, preferably 1 to 20, and more preferably 2 to 10.
  • the aspect ratio (represented by w/t as described below) is the ratio of a shorter side to a longer side in the rectangle that forms the transverse direction (TD) cross-section of a rectangular wire.
  • a rectangular wire thickness t is equal to the shorter side of the rectangle that forms the transverse direction (TD) cross-section
  • a rectangular wire width w is equal to the longer side of the rectangle that forms the transverse direction (TD) cross-section.
  • the rectangular wire thickness is generally 0.1 mm or less, preferably 0.07 mm or less, and more preferably 0.05 mm or less.
  • the rectangular wire width is generally 1 mm or less, preferably 0.7 mm or less, and more preferably 0.5 mm or less.
  • subjecting a rectangular wire to coil working in the thickness direction means that a rectangular wire is wound into a coil shape while taking the width w of the rectangular wire as the width of the coil.
  • Another embodiment of the method of producing a copper alloy wire of the present invention may be a whole production process of first subjecting a roughly-drawn rod obtained by casting to first cold-working (wire-drawing); recovering elongation by intermediate annealing; further performing second cold-working (wire-drawing) to obtain a desired wire diameter or a desired wire thickness, and controlling a predetermined mechanical strength and elongation by final (finish) annealing.
  • first cold-working wire-drawing
  • second cold-working wire-drawing
  • the respective working ratios for these first and second cold wire-drawings vary depending on the target wire diameter or wire thickness, the copper alloy composition, and the conditions for the two heating of intermediate annealing and finish-annealing, and there are no particular limitations on the working ratios. However, generally, the working ratio for the first cold-working (wire-drawing) is set to 70.0 to 99.9%, and the working ratio for the second cold-working (wire-drawing) is set to 70.0 to 99.9%.
  • a sheet or a strip having a predetermined alloy composition is produced, and the sheet or strip is slit, to obtain a rectangular wire or square wire having a desired wire width.
  • This production process for example, contains: casting; hot rolling; cold rolling; finish-annealing; and slitting. If necessary, the intermediate annealing may be carried out in the mid course of a plurality of cold rollings. Slitting may be carried out before the finish-annealing, if necessary.
  • Fig. 3 shows the changes in the physical strength (tensile strength) and elongation when a Cu-1%Ag-0.1%Mg round wire with diameter ⁇ 0.1 mm is heated at various temperatures.
  • the round wire is heated at a temperature lower than the heating-enabling temperature range, the resultant wire is high in physical strength but not sufficient in elongation exhibited, thus defects occur at the time of coil forming.
  • the round wire is heated at a temperature higher than the heating-enabling temperature range, the resultant wire is high in elongation but conspicuously low in physical strength, thus, defects may occur at the time of coil forming or fatigue resistance may be deteriorated, resulting in shortening in the service life of the coil.
  • the wire diameter or the wire thickness of the copper alloy wire of the present invention is preferably 0.1 mm or less, more preferably 0.07 mm or less, and even more preferably 0.05 mm or less.
  • the lower limit of the wire diameter or the wire thickness is generally 0.01 mm or more.
  • the use of the copper alloy wire of the present invention is not particularly limited. Examples of the use include an extra-fine magnet wire for use in speaker coils that are used in mobile telephones, smart phones, and the like.
  • the heating conditions were adjusted such that the conditions would result in an elongation that was relatively close to 13 to 18%.
  • round wire were, respectively, produced in the same manner as above, except for using the Cu-Ag-Mg-(Sn, Zn, In, Ni, Co, Zr or Cr) alloys in Examples according to this invention having the respective alloy composition, as shown in Table 2, which contained, in addition to Ag and Mg, at least one optional alloying element selected from the group consisting of Sn, Zn, In, Ni, Co, Zr, and Cr, with the balance being Cu and unavoidable impurities, and the copper alloys of Comparative examples having the respective alloy composition as shown in Table 2.
  • Table 2 which contained, in addition to Ag and Mg, at least one optional alloying element selected from the group consisting of Sn, Zn, In, Ni, Co, Zr, and Cr, with the balance being Cu and unavoidable impurities, and the copper alloys of Comparative examples having the respective alloy composition as shown in Table 2.
  • Rectangular wire samples were produced in the same manner as the above round wires, except that, after the roughly-drawn rods were subjected to cold-working (wire-drawing) or after the intermediate annealing if conducted, rectangular wire-working was carried out, and then the finish-annealing was carried out. As shown in Table 3, some samples were subjected to the intermediate annealing, and the other samples were not subjected to the intermediate annealing. Furthermore, even if the appropriate heating temperature range as defined in the present invention is adopted, the balance between elongation and physical strength varies to a large extent, depending on the heating conditions. Thus, the heating conditions were adjusted such that the conditions would result in an elongation that was relatively close to 13 to 18%.
  • TS tensile strength
  • EI elongation
  • the electrical conductivity (EC) was measured, according to JIS H0505.
  • CP MPa / mass % Tensile strength of copper wire ⁇ 350 MPa / Ag content mass %
  • the number of repeating times at breakage in bending fatigue was measured by the testing method as illustrated in Fig. 1 , and the service life of the coil was evaluated based on the number of repeating times at breakage in bending fatigue.
  • a test specimen of a copper alloy wire sample with a wire diameter ⁇ or wire thickness t of 0.04 mm (40 ⁇ m) was sandwiched between two dies, and a load was applied thereon by hanging a weight (W) of 20 g at the lower end of the specimen in order to suppress deflection (flexure) of the wire.
  • W weight
  • the sample was mounted to be sandwiched between the two dies in the wire thickness direction (ND).
  • the upper end of the specimen was fixed with a connecting jig. While having the specimen maintained in this state, the specimen was bended 90° on the left side and the right side, respectively, bending was repeatedly carried out at a speed of 100 times per minute, and the number of repeating times at breakage in bending was measured for each specimen, i.e. the respective sample. Regarding the number of repeating times in bending, one reciprocation of 1 ⁇ 2 ⁇ 3 in Fig. 1 was counted as one time, and the distance between the two dies was set to 1 mm so that the specimen of the copper alloy wire would not be compressed in the test. Determination of breakage was made such that the specimen was judged to be broken when the weight hung at the lower end of the specimen dropped.
  • the radius of bending (R) was set to 1 mm, 4 mm or 6 mm, depending on the curvature of the dies.
  • the results are evaluated in the following criterion: a specimen which gave the number of repeating times at breakage in bending of 201 times or more was rated as " ⁇ (excellent)", a specimen with the number of repeating times at breakage in bending of 151 to 200 times was rated as " ⁇ (good)”, a specimen with the number of repeating times at breakage in bending of 101 to 150 times was rated as " ⁇ (slightly poor)", and a specimen with the number of repeating times at breakage in bending of less than 100 times was rated as " ⁇ (poor)”.
  • the coil performance was evaluated in the following criterion: a sample with tensile strength less than 350 MPa or elongation less than 7% was rated as “ ⁇ (poor)", a sample with tensile strength 350 MPa or more but less than 370 MPa and elongation 7% or more was rated as “ ⁇ (good)”, and a sample with tensile strength 370 MPa or more and elongation 7% or more, and also electrical conductivity 75%IACS or more was rated as " ⁇ (excellent)”.
  • 'Temp.' means the heating temperature
  • 'Time period' means the heating time period.
  • 'Batch' means the batch-type annealing (heating)
  • 'Running' means the running-type continuous annealing (heating).
  • "Ex” means Example according to this invention
  • “C ex” means Comparative example.
  • the copper alloy wires of the present invention containing Mg each have a higher physical strength than the copper alloy wires of Comparative examples not containing Mg. Furthermore, the copper alloy wires of the present invention are comparative and are excellent, to the conventional Cu-Ag alloy wires, in view of the balance between electrical conductivity and physical strength. It is understood from these results that the copper alloy wires of the present invention can exhibit performance that is equivalent to the high concentration Cu-Ag alloy wires of Comparative examples, at smaller Ag contents and lower cost.
  • the Cu-Ag-Mg alloy wires produced according to the production method of the present invention can be heated at a temperature lower by approximately 50°C, as compared with Cu-Ag alloy wires of higher concentrations than the alloy wires of Comparative examples having physical strength of the same extent, and the cost required for the heating can be reduced to a large extent.
  • copper alloy wires having 0.5 to 2 mass% of Ag and 0.05 to 0.3 mass% of Mg are excellent in both the cost performance and the coil performance, and have properties more suitable as extra-fine magnet wires.
  • Comparative examples 6 to 15 are comparative examples of the alloy compositions respectively simulating the Patent Literature 1.
  • Comparative example 16 is a comparative example of an alloy composition simulating the Patent Literature 3
  • Comparative example 17 is a comparative example of an alloy composition simulating the Patent Literature 2.
  • those wires each have insufficient physical strength, and at least any one of the cost performance and the service life of coil is inferior. Thus, the resultant wires could not be used as extra-fine magnet wires.
  • Comparative example 18 is a comparative example which was subjected to none of intermediate annealing and finish-annealing; however, the resultant wire had insufficient elongation and could not be used as an extra-fine magnet wire.
  • Table 4 shows the results of the influence on the formability into magnet wire, when the wire diameter was changed into various values, in the Cu-Ag-Mg alloy wires (round wires) of the present invention and Comparative examples and the Cu-Ag alloy wires (round wires) of Comparative examples.
  • Table 5 shows the results, obtained: by heating Cu-Ag-Mg alloy wires according to the present invention, and Cu-Ag alloy wires and Cu-Ag-Mg alloy wires (each with an insufficient Mg content) for comparison, at any of various temperatures in the batch-type for 30 minutes; and measuring the heating temperature range, in which both a tensile strength of 350 MPa or more and an elongation of 7% or more can be obtained. It can be seen that, although the Cu-Ag-Mg alloy wires according to the present invention have lower Ag concentrations, the alloy wires have heating temperature ranges that are equal to or broader than those in conventional high concentration Cu-Ag alloy wires for comparison.
  • a semi-softening treatment by which a Cu-Ag-Mg alloy wire obtainable can achieve a balance between elongation and physical strength as desired can be carried out easily in a broader heating temperature range, and can be produced products having a stabilized performance.

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Claims (4)

  1. Fil en alliage de cuivre consistant en 0,5 à 4,0 % en masse, de préférence 0,5 à 2,0 % en masse, d'Ag, et 0,05 à 0,5 % en masse, de préférence 0,05 à 0,3 % en masse, de Mg, et éventuellement au moins l'un choisi dans le groupe constitué par Sn, Zn, In, Ni, Co, Zr et Cr en une teneur de l'élément d'alliage respectif de 0,05 à 0,3 % en masse, le reste étant du Cu et des impuretés inévitables,
    lequel fil en alliage de cuivre a une résistance à la traction de 350 MPa ou plus ; un état semi-ramolli dans lequel l'allongement est de 7 % ou plus mais de 30 % ou moins ; et une plage élargie de température de semi-ramollissement.
  2. Fil en alliage de cuivre selon la revendication 1, qui a un allongement de 10 % à 20 %.
  3. Fil en alliage de cuivre selon la revendication 1 ou 2, qui a un diamètre de fil ou une épaisseur de fil de 0,1 mm ou moins, de préférence de 50 µm ou moins.
  4. Procédé de production du fil en alliage de cuivre selon l'une quelconque des revendications 1 à 3, comprenant les étapes suivantes :
    un tréfilage consistant à soumettre un fil grossièrement étiré en un alliage de cuivre consistant en 0,5 à 4,0 % en masse, de préférence 0,5 à 2,0 % en masse, d'Ag, et 0,05 à 0,5 % en masse, de préférence 0,05 à 0,3 % en masse, de Mg, et éventuellement au moins l'un choisi dans le groupe constitué par Sn, Zn, In, Ni, Co, Zr et Cr en une teneur de l'élément d'alliage respectif de 0,05 à 0,3 % en masse, le reste étant du Cu et des impuretés inévitables, à un usinage à froid, pour former un fil ayant un diamètre de fil ou une épaisseur de film de 0,1 mm ou moins, de préférence de 50 µm ou moins ; et
    un chauffage final destiné à porter le fil dans l'état semi-ramolli, lequel chauffage final est effectué sous la forme d'un chauffage du type en discontinu à une température de 300 °C à 600 °C pendant 30 à 120 minutes ; ou d'un chauffage du type en continu à une température de 300 °C à 700 °C pendant 0,1 à 5 secondes ;
    dans lequel, lors du tréfilage, un chauffage intermédiaire est éventuellement effectué à mi-chemin d'une pluralité d'usinages à froid.
EP13812970.5A 2012-07-02 2013-07-02 Fil en alliage de cuivre, et procédé de fabrication de celui-ci Active EP2868757B1 (fr)

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PCT/JP2013/068159 WO2014007258A1 (fr) 2012-07-02 2013-07-02 Fil en alliage de cuivre, et procédé de fabrication de celui-ci

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JP6201815B2 (ja) * 2014-02-28 2017-09-27 株式会社オートネットワーク技術研究所 銅合金撚線の製造方法
WO2015152166A1 (fr) * 2014-03-31 2015-10-08 古河電気工業株式会社 Matériau de fil d'alliage de cuivre et son procédé de fabrication
CN104046842A (zh) * 2014-06-05 2014-09-17 锐展(铜陵)科技有限公司 一种汽车电子仪表用高镍铜合金线的制备方法
JP6529346B2 (ja) * 2015-06-04 2019-06-12 古河電気工業株式会社 高耐屈曲疲労性銅系合金線
CN105401044A (zh) * 2015-11-23 2016-03-16 芜湖楚江合金铜材有限公司 一种超精密加工用铜合金线材及其制备方法
CN105603242B (zh) * 2015-12-21 2018-03-23 赣州江钨拉法格高铁铜材有限公司 一种铜银镁合金接触线及其制备方法
EP3460080B1 (fr) 2016-05-16 2021-01-06 Furukawa Electric Co., Ltd. Matériau de fil en alliage de cuivre
WO2022202871A1 (fr) * 2021-03-23 2022-09-29 古河電気工業株式会社 Fil d'alliage de cuivre
CN113560365B (zh) * 2021-07-22 2023-08-15 诺克威新材料(江苏)有限公司 一种提高铜合金拉丝强度的加工方法
CN114369735A (zh) * 2021-12-16 2022-04-19 虹华科技股份有限公司 一种电子芯片用高纯铜铜丝的加工工艺

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JPH02243733A (ja) 1989-03-15 1990-09-27 Fujikura Ltd 銅合金線材
JPH0477060A (ja) 1990-07-16 1992-03-11 Minolta Camera Co Ltd 画像形成装置
JP3941304B2 (ja) * 1999-11-19 2007-07-04 日立電線株式会社 超極細銅合金線材及びその製造方法並びにこれを用いた電線
JP3948203B2 (ja) * 2000-10-13 2007-07-25 日立電線株式会社 銅合金線、銅合金撚線導体、同軸ケーブル、および銅合金線の製造方法
JP4143010B2 (ja) * 2003-09-16 2008-09-03 日立電線株式会社 銅合金導体の製造方法
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JP5195019B2 (ja) 2008-05-21 2013-05-08 住友電気工業株式会社 Ｃｕ−Ａｇ合金線、巻線、及びコイル

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EP2868757A1 (fr) 2015-05-06
JPWO2014007258A1 (ja) 2016-06-02
WO2014007258A1 (fr) 2014-01-09
EP2868757A4 (fr) 2016-04-27
JP5840234B2 (ja) 2016-01-06
CN104169448B (zh) 2017-10-24
CN104169448A (zh) 2014-11-26
KR20150030188A (ko) 2015-03-19
KR101719888B1 (ko) 2017-03-24

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