WO2014007259A1 - 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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Publication number
WO2014007259A1
WO2014007259A1 PCT/JP2013/068160 JP2013068160W WO2014007259A1 WO 2014007259 A1 WO2014007259 A1 WO 2014007259A1 JP 2013068160 W JP2013068160 W JP 2013068160W WO 2014007259 A1 WO2014007259 A1 WO 2014007259A1
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Prior art keywords
wire
copper alloy
heat treatment
elongation
copper
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PCT/JP2013/068160
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English (en)
Japanese (ja)
Inventor
司 ▲高▼澤
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古河電気工業株式会社
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Application filed by 古河電気工業株式会社 filed Critical 古河電気工業株式会社
Priority to JP2013554707A priority Critical patent/JP5840235B2/ja
Priority to KR1020147026828A priority patent/KR101719889B1/ko
Priority to CN201380015337.3A priority patent/CN104169447B/zh
Priority to EP13813342.6A priority patent/EP2868758B1/fr
Publication of WO2014007259A1 publication Critical patent/WO2014007259A1/fr

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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 for manufacturing the same, and more particularly to an ultrafine copper alloy wire for a magnet wire and a method for manufacturing the same.
  • a coil for a microspeaker used in a mobile phone, a smartphone, or the like is manufactured by winding an extra fine wire (magnet wire) having a wire diameter of 0.1 mm or less into a coil shape.
  • This winding processing requires toughness (elongation) as the workability that allows the formation of turns, and conventionally pure copper having excellent toughness has been used.
  • pure copper is excellent in electrical conductivity, it has a low strength, so there is a problem that fatigue resistance accompanying coil vibration is low.
  • Patent Document 1 a technique using a high concentration Cu—Ag alloy containing 2 to 15 mass% of Ag that can increase the tensile strength without decreasing the conductivity.
  • a processed metal or alloy has an increased tensile strength and a reduced elongation.
  • a heat treatment at a certain temperature or higher is applied thereto, the elongation is restored and the strength is decreased.
  • Patent Document 2 a technique has been proposed in which the strength and elongation are compatible even with a low-concentration alloy by performing the heat treatment temperature below the softening temperature.
  • a technique has been proposed in which compressive stress is applied by applying surface processing to a ⁇ 2.6 mm annealed copper alloy wire having an electrical conductivity of 98% IACS or more to improve the bending fatigue resistance.
  • JP 2009-280860 A Japanese Patent No. 3944304 JP 05-86445 A
  • Patent Document 3 when an attempt is made to apply surface processing to the technique of Patent Document 3 for an annealed copper wire or copper alloy wire having a diameter of 0.1 mm or less, an annealed copper wire or copper alloy wire having a diameter of 0.1 mm or less is disclosed in Patent Document 3. Since the wire diameter is remarkably smaller than that of the described copper alloy wire, the strength of the copper alloy wire itself is low, and the wire itself is disconnected due to a load during processing, making the processing itself difficult. Recently, the shape of the magnet wire is not limited to a round wire, and the use of a square wire or a flat wire is also being studied. Also in the case of these square wires and flat wires, it is required that the wire be thin enough to correspond to the diameter of the round wire.
  • the present invention has been made in view of such problems in the prior art, and has an object to provide a copper alloy wire rod excellent in elongation and bending fatigue resistance, for example, suitably used for, for example, a magnet wire at a low cost.
  • the present inventors diligently studied various copper alloys, their heat treatments and processing conditions in order to develop copper alloy wires suitable for use in magnet wires having excellent elongation and bending fatigue resistance.
  • the wire material is subjected to cold working at a constant light working rate on the surface of the wire, thereby keeping the surface shallow from the surface of the wire.
  • a copper alloy wire excellent in elongation and bending fatigue resistance can be obtained by raising the hardness within a range.
  • the present invention has been completed based on this finding.
  • the following means are provided.
  • the copper alloy wire according to item (1) containing 0.5 to 4% by mass of Ag.
  • Item (1) comprising at least one selected from the group consisting of Sn, Mg, Zn, In, Ni, Co, Zr, and Cr as a content of 0.05 to 0.3% by mass.
  • the copper alloy wire described in 1. (4) 0.05 to 4 mass% of Ag, and 0.05 to 0 as the content of each of at least one selected from the group consisting of Sn, Mg, Zn, In, Ni, Co, Zr and Cr .
  • a method of producing a copper alloy wire comprising a cold working step of performing cold working at a working rate of 3 to 15% on the heat treated wire.
  • the obtained copper alloy wire has a nanoindentation hardness of 1.45 GPa or more in a depth region between the outermost surface of the wire and at least 5% inside with respect to the wire diameter or wire thickness, and A method for producing a copper alloy wire, wherein the nanoindentation hardness of the central portion of the wire is less than 1.45 GPa, the wire has a tensile strength of 350 MPa or more and an elongation of 7% or more.
  • an intermediate heat treatment is performed between a plurality of cold processing so that the wire after the intermediate heat treatment has a tensile strength of 330 MPa or more and an elongation of 10% or more. Manufacturing method of copper alloy wire.
  • the semi-softened state means a state in which the elongation of the copper alloy wire satisfies 10% or more, preferably 10% to 30%.
  • Semi-softening treatment refers to heat treatment that gives the semi-softening state.
  • the softened state means a state in which the elongation of the copper alloy wire has been recovered by exceeding 30%.
  • the softening treatment refers to a heat treatment at a high temperature that gives the softened state.
  • the wire means a square wire or a flat wire in addition to the round wire. Accordingly, the wire of the present invention refers to a round wire, a square wire, and a flat wire unless otherwise specified.
  • the size of the wire is a round wire (the cross section in the width direction (TD) is circular), the wire diameter ⁇ (the diameter of the circle in the cross section) of the round wire, and a square (the cross section in the width direction is a square).
  • Is the thickness t and width w of the square wire both are the same as the length of one side of the square of the cross section), and if it is a flat wire (the cross section in the width direction is rectangular), the thickness of the flat wire It refers to the length t (the length of the short side of the rectangle of the cross section) and the width w (the length of the long side of the rectangle of the cross section).
  • the copper alloy wire of the present invention is suitable as, for example, a copper alloy wire for a magnet wire because it has excellent bending fatigue resistance while having elongation required for coil forming. Furthermore, the method for producing a copper alloy wire of the present invention is suitable as a method for producing a copper alloy wire having excellent performance.
  • the nanoindentation hardness in the region is 1.45 GPa or more.
  • the nanoindentation hardness in the depth region between the outermost surface of the wire and the inside of the wire diameter or wire thickness up to 20% at the maximum can be 1.45 GPa or more.
  • the nanoindentation hardness in the depth region between the outermost surface of the wire and the inside of the wire diameter or the wire thickness by 15% is 1.45 GPa or more.
  • the region having the specific nanoindentation hardness is formed so as to have the hardness by work hardening in the final (finishing) processing performed after the final heat treatment that gives a semi-softened state.
  • a specific depth region on the surface of the wire formed by such processing is also referred to as “surface processed layer” or “wire surface portion”.
  • the nano-indentation hardness is less than 1.45 GPa at the center of the wire, and the entire wire is not hardened like the wire surface portion.
  • the reason why the region having a nanoindentation hardness of 1.45 GPa or more from the outermost surface of the wire to the inside of the wire diameter or the wire thickness is up to 20% is the deeper region beyond this ( This is because if the wire is cured to the more central side), sufficient elongation cannot be secured.
  • the wire is not cured in a semi-softened state as a result of the final heat treatment.
  • the nanoindentation hardness inside the surface processed layer (typically the central part of the wire) is usually less than 1.45 GPa, and preferably 1.3 GPa or less in order to ensure sufficient elongation.
  • the nanoindentation hardness is a method of measuring the hardness of a minute region called the nanoindentation method. A triangular pyramid diamond indenter is pushed from the surface of the (wire) sample, the load applied at that time, and the indenter And the hardness obtained from the contact projected area of the sample.
  • Non-Patent Document 1 Metal, Vol. 78 (2008) No. 9, p. 47
  • the wire material surface portion is formed as a work-hardened surface processed layer, and the nanoindentation hardness in the wire material surface portion is preferably 1.5 GPa or more. The bending fatigue resistance can be further improved.
  • a depth region in which the thickness of the surface processed layer having a predetermined nanoindentation hardness of 1.5 GPa or more is from the outermost surface of the wire to the inside of the wire diameter or wire thickness by at least 5%. (Maximum depth region up to 20% inside, preferably 15% inside depth region) If the elongation of the entire copper alloy wire can also exhibit good characteristics of 10% or more, A more excellent magnet wire can be obtained.
  • the nanoindentation hardness in the surface portion of the wire is 1.45 GPa or more, more preferably 1.6 GPa or more. Although there is no restriction
  • the copper alloy wire of the present invention has (i) 0.5 to 4% by mass of Ag and / or (ii) at least one selected from the group consisting of Sn, Mg, Zn, In, Ni, Co, Zr and Cr.
  • the content of each seed is 0.05 to 0.3% by mass, and the balance is made of Cu and inevitable impurities.
  • the content of the alloy additive element is simply “%”, it means “mass%”.
  • the total content of at least one alloy component selected from the group consisting of Sn, Mg, Zn, In, Ni, Co, Zr and Cr other than Ag is preferably 0.5% by mass or less. is there.
  • (i) Ag may be contained alone, or (ii) at least one selected from the group consisting of Sn, Mg, Zn, In, Ni, Co, Zr and Cr.
  • the seed may be contained alone, or both (i) Ag and (ii) at least one selected from the group consisting of Sn, Mg, Zn, In, Ni, Co, Zr and Cr. You may contain.
  • These elements are solid solution strengthening type or precipitation strengthening type elements, respectively, and by adding these elements to Cu, the strength can be increased without significantly lowering the conductivity.
  • This addition increases the strength of the copper alloy wire itself and improves the bending fatigue resistance, and after heat-treating (semi-softening treatment) after processing the wire diameter or wire thickness into an ultrafine wire of 0.1 mm or less. However, it can withstand the final (finish) cold working for curing the surface portion of the wire after the semi-softening treatment.
  • the bending fatigue resistance is proportional to the tensile strength, but if processing is performed in order to increase the tensile strength, the elongation decreases and it becomes impossible to form into an ultrafine copper alloy wire such as a magnet wire.
  • the bending strain applied to the copper alloy wire during bending fatigue is larger at the outer peripheral portion of the wire, and the bending strain is smaller as it is closer to the center portion. Therefore, according to the present invention, the bending fatigue resistance can be improved by work hardening so that only a predetermined depth region (the wire surface portion) on the surface of the wire has a predetermined hardness by finish cold working. it can. In addition, only the wire surface portion is work-hardened, but the entire remaining wire portion other than the wire surface portion (that is, the portion other than the wire surface portion to the center deeper than the predetermined depth) maintains a semi-softened state. is doing. For this reason, since the elongation as a whole wire can be secured sufficiently, it becomes possible to form an ultrafine copper alloy wire such as a magnet wire.
  • the Ag is an element that can increase the strength without lowering the electrical conductivity, among these elements, and is an example of an essential additive element in the copper alloy according to the present invention used for, for example, a magnet wire.
  • the Ag content is 0.5 to 4% by mass, preferably 0.5 to 2%. If the Ag content is too low, sufficient strength cannot be obtained. Moreover, when there is too much Ag content, while electroconductivity will fall, cost will become high too much.
  • At least one element selected from the group consisting of Sn, Mg, Zn, In, Ni, Co, Zr, and Cr is another example of the essential additive element in the copper alloy according to the present invention.
  • the content of these elements is 0.05 to 0.3%, preferably 0.05 to 0.2% as each content. When this content is too small as each content, the effect of the strength increase by addition of these elements is hardly expected. Further, if the content is too large, the decrease in conductivity is too large, so that it is not suitable as a copper alloy wire such as a magnet wire.
  • the manufacturing method of the copper alloy wire of the present invention will be described.
  • the shape of the copper alloy wire of the present invention is not limited to a round wire, and may be a square wire or a flat wire, which will be described below.
  • the copper alloy round wire manufacturing method according to the present invention includes, for example, casting, intermediate cold working, intermediate heat treatment (intermediate annealing), final heat treatment (final annealing), and finish cold working. It is given in order.
  • intermediate annealing may be omitted.
  • a graphite crucible is used for melting and casting.
  • the atmosphere inside the casting machine when melting is preferably a vacuum or an inert gas atmosphere such as nitrogen or argon in order to prevent the formation of oxides.
  • a horizontal type continuous casting machine, an Upcast method, etc. can be used.
  • the steps from casting to wire drawing are continuously performed to cast a rough drawn wire having a diameter of usually about ⁇ 8 to 23 mm.
  • a billet (ingot) obtained by casting is subjected to wire drawing to obtain a rough drawing wire having a diameter of usually about ⁇ 8 to 23 mm.
  • the first and second cold working Intermediate annealing may be performed during this period.
  • the heat treatment method for performing the intermediate annealing is roughly classified into a batch type and a continuous type. Batch-type heat treatment is inferior in productivity because it takes processing time and cost, but it is easy to control characteristics because temperature and holding time are easy to control.
  • continuous heat treatment is excellent in productivity because it can be performed continuously with the wire drawing process, but since heat treatment needs to be performed in an extremely short time, the heat treatment temperature and time are accurately controlled to stabilize the characteristics. It needs to be realized.
  • a heat treatment method suitable for the purpose may be selected.
  • the heat treatment it is preferable to perform the heat treatment at 300 to 600 ° C. for 30 minutes to 2 hours in a heat treatment furnace in an inert atmosphere such as nitrogen or argon.
  • the continuous heat treatment include an electric heating method and an in-atmosphere heat treatment method.
  • the electric heating method is a method in which an electrode ring is provided in the middle of the wire drawing process, a current is passed through the copper alloy wire passing between the electrode wheels, and heat treatment is performed by Joule heat generated in the copper alloy wire itself.
  • a heating container is provided in the middle of wire drawing, and the copper alloy wire is passed through the heating container atmosphere heated to a predetermined temperature (for example, 300 to 700 ° C.) to perform the heat treatment.
  • a predetermined temperature for example, 300 to 700 ° C.
  • the heat treatment is preferably performed in an inert gas atmosphere in order to prevent oxidation of the copper alloy wire.
  • the heat treatment conditions in these continuous heat treatments are preferably 300 to 700 ° C. and 0.5 to 5 seconds.
  • the tensile strength of the copper alloy wire after the intermediate heat treatment satisfies the characteristics of 330 MPa or more and elongation of 10% or more.
  • a heat treatment method for performing the finish annealing a batch method and a continuous method can be used as in the case of the intermediate annealing.
  • the finish annealing depending on the composition and processing rate of the copper alloy wire, the tensile strength and elongation of the wire after the final heat treatment may change slightly. Therefore, in the present invention, the heating temperature and heating holding time in finish annealing are appropriately adjusted so that the tensile strength of the copper alloy wire obtained by this final heat treatment (finish annealing) is 330 MPa or more and the elongation is 10% or more. To do.
  • the heat treatment is performed in a shorter time as the heat treatment temperature is higher, and the heat treatment is performed in a longer time as the heat treatment temperature is lower.
  • finish annealing when finish annealing is performed in a batch system, it is preferable to perform heat treatment at 300 to 450 ° C. for 30 minutes to 2 hours.
  • the properties of the copper alloy wire before final annealing are adjusted so that the final properties of the copper alloy wire obtained by finish cold working after this final annealing will be a tensile strength of 350 MPa or more and an elongation of 7% or more. And final annealing conditions are determined.
  • the bending strain applied to the line at the time of bending fatigue is larger toward the outer periphery of the line, and the amount of bending strain is smaller as it is closer to the center. Therefore, the bending fatigue resistance can be improved by performing finish cold working and hardening only the surface portion of the wire.
  • the center side of the wire is maintained in a semi-softened state, so that the entire wire can be sufficiently stretched and formed into an ultrafine wire such as a magnet wire. Is also possible.
  • the risk of disconnection is effectively obtained by performing a semi-softening heat treatment that gives a strength of 350 MPa or more and an elongation of 7% or more in the final product copper alloy wire. Can be lowered.
  • the processing rate of this wire drawing is usually 3 to 15%, preferably 5 to 15%, and more preferably 7 to 12%.
  • the finish cold working rate is too small, surface processing and strength may be insufficient, and the effect of improving the bending fatigue resistance may be insufficient.
  • the work rate of this finish cold work is too large, the work may extend over the entire surface of the wire beyond the surface of the wire, which may impair the elongation and increase the risk of disconnection in the work.
  • the method for producing a copper alloy rectangular wire of the present invention is the same as the method for producing a round wire, except that it has a rectangular wire processing step and finish cold working suitable for a rectangular shape.
  • the method for producing a flat wire rod according to the present invention includes, for example, each step of casting, intermediate cold working (cold drawing), flat wire processing, final heat treatment (final annealing), and finish cold working. It is given in order. If necessary, intermediate annealing (intermediate heat treatment) may be inserted between the intermediate cold working and the flat wire processing, similarly to the method for producing the round wire.
  • the conditions of processing and heat treatment in each step of casting, cold working, intermediate annealing, and final annealing, and preferred conditions thereof are the same as in the method of manufacturing the round wire.
  • the rolling reduction and the total rolling reduction in each pass during rolling or the like are not particularly limited, and may be set as appropriate so that a desired rectangular wire size can be obtained.
  • the rolling reduction is the rate of change in the thickness in the rolling direction when flattening is performed, and the rolling reduction when the thickness before rolling is t 1 and the thickness of the line after rolling is t 2. (%) Is represented by ⁇ 1- (t 2 / t 1 ) ⁇ ⁇ 100.
  • the total rolling reduction can be 10 to 90%, and the rolling reduction in each pass can be 10 to 50%.
  • the cross-sectional shape of the rectangular wire is not particularly limited, but the aspect ratio is usually 1 to 50, preferably 1 to 20, and more preferably 2 to 10.
  • the aspect ratio (expressed as w / t below) is the ratio of the short side to the long side of the rectangle forming the cross-section (TD) cross section of the flat wire.
  • the thickness t of the flat wire is equal to the short side of the rectangle forming the width direction (TD) cross section
  • the width w of the flat wire is the length of the rectangle forming the cross section of the width direction (TD). Equal to edge.
  • the thickness of the flat wire is usually 0.1 mm or less, preferably 0.08 mm or less, more preferably 0.06 mm or less.
  • the width of the flat wire is usually 1 mm or less, preferably 0.7 mm or less, more preferably 0.5 mm or less.
  • the finish cold work is performed in the same manner as the flat wire processing. By this finish cold working, it is hardened so that the nanoindentation hardness of the surface portion of the wire becomes 1.45 GPa or more. The same as in the case of a round wire.
  • the finish cold working for the rectangular wire is cold rolling with a rolling mill and cold rolling with a cassette roller die. This processing rate is usually 3 to 15%, preferably 5 to 15%, more preferably 7 to 12%. When the finish cold working rate is too small, surface processing and strength may be insufficient, and the effect of improving the bending fatigue resistance may be insufficient.
  • a flat wire manufactured by such processing and heat treatment is a region of at least 5% depth from the surface of the wire on the upper and lower surface layers in the thickness direction by finish cold working (up to 20% depth from the wire surface).
  • a hardened layer having a nanoindentation hardness of 1.45 GPa or more is provided as a surface processed layer in a region (preferably a region from the surface of the wire to a depth of 15%).
  • the hardened layer exists as a surface-treated layer on the entire surface in the circumferential direction of the wire, whereas in the case of a flat wire, the both sides of the surface of the wire in the thickness direction are respectively The difference is that the hardened layer exists as a surface processed layer.
  • the point which has the said hardened layer as a surface processing layer in the surface part of a wire within the predetermined shallow range it is the same with a round wire and a flat wire (and also a square wire).
  • winding a flat wire in the thickness direction means winding the flat wire in a coil shape with the width w of the flat wire being the width of the coil.
  • Each of the processing rates in the first and second cold wire drawing processes varies depending on the target wire diameter or wire thickness and copper alloy composition, as well as two heat treatment conditions of intermediate annealing and finish annealing.
  • the processing rate in the first cold working (drawing) is usually set to 70.0 to 99.9%, and the processing rate in the second cold working (drawing). Is 70.0 to 99.9%.
  • a plate material or strip material having a predetermined alloy composition can be manufactured, and these plates or strips can be slit to obtain a rectangular wire material or a rectangular wire material having a desired line width.
  • this manufacturing process for example, there is a method comprising casting, hot rolling, cold rolling, finish annealing, finish cold working, and slitting. If necessary, intermediate annealing may be performed during the cold rolling. In some cases, the slitting may be performed before finish annealing or before finish cold working.
  • the wire diameter or the wire thickness of the copper alloy wire of the present invention is 0.1 mm or less, preferably 0.08 mm or less, more preferably 0.06 mm or less.
  • the lower limit of the wire diameter or the wire thickness is not particularly limited, but is usually 0.01 mm or more in the current technology.
  • the use of the copper alloy wire of the present invention is not particularly limited, and examples thereof include a magnet wire that is an extra fine wire used for a speaker coil used in a mobile phone, a smartphone, and the like.
  • the reason why the tensile strength of the copper alloy wire of the present invention is set to 350 MPa or more is that when it is less than 350 MPa, the strength when the diameter is reduced by wire drawing is insufficient, and the bending fatigue resistance is inferior. Further, the reason why the elongation of the copper alloy wire of the present invention is set to 7% or more is that if it is less than 7%, the workability is inferior and problems such as breakage occur when the coil is formed.
  • the copper alloy wire of the present invention obtained by the above method exhibits high bending fatigue resistance while having elongation that can be formed as an ultrafine copper alloy wire such as an ultrafine wire magnet wire.
  • the cast material is composed of 0.5 to 4% by mass of Ag and / or 0.05 to 0.3% by mass of Sn, Mg, Zn, In, Ni, Co, Zr, and Cr as respective contents.
  • Copper alloys of the present invention having various alloy compositions shown in Tables 1 to 3 containing at least one selected from the group, with the balance being Cu and inevitable impurities, and various alloys shown in Tables 1 to 3 A comparative copper alloy having a composition was cast into a rough drawn wire having a diameter of 10 mm by a horizontal continuous casting method.
  • This rough drawn wire is subjected to cold working (drawing), intermediate annealing, finish annealing, finish cold working (drawing) (total working rate of the following first and second cold workings: 99.984%
  • total working rate of the following first and second cold workings 99.984%
  • round wire samples having a final wire diameter of 40 ⁇ m and in the test examples of Table 2 having various wire diameters shown in the table were prepared.
  • the heat treatment of intermediate annealing and finish annealing was performed in any of three patterns selected from batch annealing, current annealing, and running annealing, and each was performed in a nitrogen atmosphere.
  • the intermediate annealing was performed only once between the first cold working (drawing) and the second cold working (drawing).
  • Examples of rectangular wires, comparative examples In the same manner as the round wire, except that after roughing the wire (drawn), or after intermediate annealing in the case of carrying out, after performing the rectangular wire processing, after finishing annealing, Finished cold working was performed to prepare a rectangular wire sample. As shown in Table 4, there are those that have been subjected to intermediate annealing and those that have not. As shown in Table 4, the flat wire processing is performed by cold rolling the wire diameter ⁇ (mm) of the unprocessed round wire into a flat wire having a size of width w (mm) ⁇ thickness t (mm). processed. The finish cold working was performed by cold rolling in the same manner as the flat wire processing except that the processing rates shown in Table 4 were used. Table 4 shows the production conditions of the copper alloy rectangular wire according to the present invention and the copper alloy rectangular wire of the comparative example and the characteristics of the obtained copper alloy rectangular wire.
  • the upper end of the sample was fixed with a connector.
  • the sample was bent 90 degrees to the left and right, repeatedly bent at a rate of 100 times per minute, and the number of bending until breaking was measured for each sample.
  • the number of bendings was counted as one round trip of 1 ⁇ 2 ⁇ 3 in the figure, and the interval between the two dies was set to 1 mm so as not to press the copper alloy wire sample during the test.
  • the determination of breakage was made when the weight suspended at the lower end of the sample dropped.
  • the bending radius (R) was set to 2 mm depending on the curvature of the die.
  • the coil life was evaluated by the number of bending fatigue fractures measured by the above test method as follows.
  • the hardness of the surface of the wire and the center of the wire was measured using a nanoindenter (ENT-2100 manufactured by Elionix).
  • the thickness ( ⁇ m) of the processed layer on the surface side of the wire is obtained from the structure observation of the wire cross section (TD cross section) and the hardness change in the nanoindenter test, and the “surface processed layer thickness ( ⁇ m)” It was. Further, from the obtained thickness ( ⁇ m) of the processed layer, the ratio (%) of the thickness from the outermost surface of the wire to the most central side of the processed layer with respect to the wire diameter ⁇ of the wire or the thickness t of the wire is calculated. It was determined as “surface processed layer thickness (%)”.
  • the coil formability was determined by testing the frequency of occurrence of disconnection when a copper alloy wire 100 km was wound into a coil having a diameter of 5 mm, and “ ⁇ (good)” that was not disconnected once. Was evaluated as “C (slightly inferior)” and “ ⁇ (defect)” when the wire was broken twice or more.
  • Table 1 shows a sample of the round wire rods of Examples of the present invention (Examples 1 to 6) and a sample of the round wire rod of the comparative example in which a Cu-2% Ag alloy wire was processed and heat-treated so as to have a final wire diameter of 0.04 mm ( ⁇ 40 ⁇ m).
  • the results of measuring and evaluating the characteristics of (Comparative Examples 1 to 7) are shown.
  • the final heat treatment (finish annealing) conditions were changed as shown in Table 1, and the strength and elongation before finish cold working were variously changed.
  • finish cold working at a processing rate of 3 to 15% is applied to the copper alloy wire that has been subjected to final heat treatment (finish annealing) so that the tensile strength is 330 MPa or more and the elongation is 10% or more.
  • finish annealing finish annealing
  • a processed layer having a nanoindentation hardness of 1.45 GPa or more was formed on the surface portion of the wire, and it was found that the bending fatigue resistance could be improved.
  • the finish cold working rate is 7 to 12% because the effect of improving the bending fatigue resistance is more excellent.
  • the processing rate in the finish cold work is less than 3%. If it is too small, there is no processed layer at all or the thickness of the processed layer is too thin to improve the bending fatigue resistance.
  • the processing rate in the finish cold working is larger than 15% as in Comparative Examples 4 and 5, not only the surface portion of the wire but also the processing to the entire copper alloy wire including the center side and Therefore, the surface processed layer that improves the bending fatigue resistance is not satisfactorily formed, the elongation of the copper alloy wire after the finish cold working is inferior, and the bending fatigue resistance cannot be improved.
  • Comparative Example 6 when the final heat treatment before the finish cold working is insufficient and the elongation is less than 10%, the elongation of the copper alloy wire after the finish cold working becomes less than 7% and the coil formability is insufficient. End up. Further, as shown in Comparative Example 7, when the final heat treatment before finish cold working is excessively softened and the tensile strength of the copper alloy wire is less than 330 MPa, the hardness of the wire surface portion is insufficient, and the strength after finish annealing Is also lacking. Furthermore, disconnection at the time of finish cold working will be invited. In the case of a rectangular wire, the same result as in the case of the round wire is obtained.
  • Example 7 to 12 and Comparative Examples 8 to 9 the final heat treatment (finish annealing) conditions were changed as shown in Table 2, and various diameters of Cu— were obtained with various changes in strength before finish cold working.
  • the result of having evaluated the wire drawing property when a 1% Ag alloy round wire rod is finish cold worked at a working rate of 10% is shown.
  • Comparative Examples 10 to 11 tests were performed in the same manner as described above except that a Cu-0.3% Ag alloy round wire was used instead of the Cu-1% Ag alloy wire.
  • a test of finishing a 100 km length of a soft or semi-softened copper alloy wire was performed five times, and “ ⁇ (good)” that was able to be drawn without being disconnected once was disconnected once.
  • the copper alloy wire rod preferably has a tensile strength of 330 MPa or more. Therefore, it can be seen that the bending fatigue resistance can be improved by subjecting a fine wire having a diameter of 0.1 mm or less to surface processing according to the manufacturing conditions specified by the manufacturing method of the present invention. In the case of a rectangular wire, the same result as in the case of the round wire is obtained.
  • Table 3 shows examples of the present invention and comparative examples of round wires prepared with copper alloys having various other alloy compositions.
  • the nanoindentation hardness in the depth region between the outermost surface of the wire and the inside of the wire diameter at least 5% is 1.45 GPa or more, And it turns out that a desired physical property can be achieved when the tensile strength of the final wire is 350 MPa or more and the elongation is 7% or more.
  • Table 4 shows examples of the present invention and comparative examples of rectangular wires prepared with copper alloys having various alloy compositions. From Table 4, it can be seen that the same results as in the case of the round wire were obtained in the case of the flat wire.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Metal Extraction Processes (AREA)
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Abstract

L'invention concerne un fil en alliage de cuivre qui présente un diamètre ou une épaisseur de 0,1mm au plus, et qui possède une composition en alliage comprenant 0,5 à 4% en masse d'Ag, et 0,05 à 0,3% en masse, en teneur individuelle, d'au moins un élément choisi dans un groupe constitué de Sn, Mg, Zn, In, Ni, Co, Zr et Cr, le reste étant constitué de Cu et des impuretés inévitables. Selon l'invention, la dureté de nanoindentation dans une région de profondeur allant de la surface du fil à au moins 5% vers l'intérieur du diamètre ou de l'épaisseur du fil, est de 1,45GPa au moins, tandis que la dureté de nanoindentation dans une partie centrale du fil est inférieure à 1,45GPa, la résistance à la traction du fil est de 350MPa au moins, et l'extension d'au moins 7%. Ainsi, l'invention fournit à bas coût un fil en alliage de cuivre qui se révèle excellent en termes d'extension et de caractéristiques de résistance à la fatigue par flexion, et qui peut être mis en œuvre dans un fil de bobinage, ou similaire.
PCT/JP2013/068160 2012-07-02 2013-07-02 Fil en alliage de cuivre, et procédé de fabrication de celui-ci WO2014007259A1 (fr)

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JP2013554707A JP5840235B2 (ja) 2012-07-02 2013-07-02 銅合金線材及びその製造方法
KR1020147026828A KR101719889B1 (ko) 2012-07-02 2013-07-02 구리합금 선재 및 그의 제조방법
CN201380015337.3A CN104169447B (zh) 2012-07-02 2013-07-02 铜合金线材及其制造方法
EP13813342.6A EP2868758B1 (fr) 2012-07-02 2013-07-02 Fil en alliage de cuivre, et procédé de fabrication de celui-ci

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JP2012148920 2012-07-02
JP2012-148920 2012-07-02

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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
CN106029930A (zh) * 2014-02-28 2016-10-12 株式会社自动网络技术研究所 铜合金绞线及其制造方法、汽车用电线
JP2019500494A (ja) * 2015-12-02 2019-01-10 ヘレウス マテリアルズ シンガポール ピーティーイー． リミテッド 銀合金化銅ワイヤ
CN114406228A (zh) * 2022-01-10 2022-04-29 营口理工学院 一种凝固过程中形成纳米铬相的铜合金铸件及铸造方法
US11404181B2 (en) 2020-02-06 2022-08-02 Hitachi Metals, Ltd. Copper alloy wire, plated wire, electrical wire and cable

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CN105420534A (zh) * 2015-11-06 2016-03-23 广西南宁智翠科技咨询有限公司 一种超高导电率的合金导线
CN105274389A (zh) * 2015-11-06 2016-01-27 广西南宁智翠科技咨询有限公司 一种低电阻的铜合金导线
CN105624460B (zh) * 2015-12-29 2017-10-31 陕西通达电缆制造有限公司 一种高导电率高韧性的铜合金电缆导线及其制备方法
EP3460080B1 (fr) 2016-05-16 2021-01-06 Furukawa Electric Co., Ltd. Matériau de fil en alliage de cuivre
CN108359837B (zh) * 2018-03-16 2019-08-02 重庆鸽牌电工材料有限公司 一种高纯无氧高含银铜杆的制备方法
KR20200129027A (ko) * 2018-03-20 2020-11-17 후루카와 덴키 고교 가부시키가이샤 구리 합금 선재 및 구리 합금 선재의 제조 방법
CN108777180A (zh) * 2018-05-10 2018-11-09 保定维特瑞光电能源科技有限公司 一种基于动态交通流量监测的地磁感应线圈及其制备方法

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Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106029930A (zh) * 2014-02-28 2016-10-12 株式会社自动网络技术研究所 铜合金绞线及其制造方法、汽车用电线
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
CN106164306A (zh) * 2014-03-31 2016-11-23 古河电气工业株式会社 铜合金线材及其制造方法
JPWO2015152166A1 (ja) * 2014-03-31 2017-04-13 古河電気工業株式会社 銅合金線材及びその製造方法
EP3128019A4 (fr) * 2014-03-31 2018-06-27 Furukawa Electric Co. Ltd. Matériau de fil d'alliage de cuivre et son procédé de fabrication
JP2019500494A (ja) * 2015-12-02 2019-01-10 ヘレウス マテリアルズ シンガポール ピーティーイー． リミテッド 銀合金化銅ワイヤ
US11404181B2 (en) 2020-02-06 2022-08-02 Hitachi Metals, Ltd. Copper alloy wire, plated wire, electrical wire and cable
CN114406228A (zh) * 2022-01-10 2022-04-29 营口理工学院 一种凝固过程中形成纳米铬相的铜合金铸件及铸造方法

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CN104169447A (zh) 2014-11-26
JPWO2014007259A1 (ja) 2016-06-02
JP5840235B2 (ja) 2016-01-06
KR101719889B1 (ko) 2017-03-24
EP2868758B1 (fr) 2018-04-18
EP2868758A4 (fr) 2016-05-25
EP2868758A1 (fr) 2015-05-06
KR20150034678A (ko) 2015-04-03
CN104169447B (zh) 2017-03-01

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