[go: up one dir, main page]

WO2005028143A1 - Moule de coulage et procede de coulage en continu pour alliage de cuivre - Google Patents

Moule de coulage et procede de coulage en continu pour alliage de cuivre Download PDF

Info

Publication number
WO2005028143A1
WO2005028143A1 PCT/JP2004/013756 JP2004013756W WO2005028143A1 WO 2005028143 A1 WO2005028143 A1 WO 2005028143A1 JP 2004013756 W JP2004013756 W JP 2004013756W WO 2005028143 A1 WO2005028143 A1 WO 2005028143A1
Authority
WO
WIPO (PCT)
Prior art keywords
alloy
mold
metal
piece
self
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2004/013756
Other languages
English (en)
Japanese (ja)
Inventor
Yasuhiro Maehara
Mitsuharu Yonemura
Keiji Nakajima
Naotsugu Yoshida
Masahiro Aoki
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
Original Assignee
Sumitomo Metal Industries Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Sumitomo Metal Industries Ltd filed Critical Sumitomo Metal Industries Ltd
Priority to JP2005514086A priority Critical patent/JP4333881B2/ja
Priority to EP04787939A priority patent/EP1688198A4/fr
Publication of WO2005028143A1 publication Critical patent/WO2005028143A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/14—Plants for continuous casting
    • B22D11/143—Plants for continuous casting for horizontal casting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • B22D11/004—Copper alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
    • B22D11/059—Mould materials or platings
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • 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
    • 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
    • C22C9/02—Alloys based on copper with tin as the next major constituent
    • 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
    • C22C9/04—Alloys based on copper with zinc as the next major constituent
    • 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
    • C22C9/10—Alloys based on copper with silicon as the next major constituent

Definitions

  • the present invention relates to a continuous manufacturing method and a continuous manufacturing method for a Cu alloy.
  • the present invention relates to a ⁇ type used in a direct connection type continuous forming machine in which a holding furnace is directly connected to a ⁇ type, and a continuous manufacturing method of a Cu alloy using the ⁇ type.
  • the IT boom has been used in electrical and electronic components such as lead frames, terminals, connectors, springs, and contact elements in the movement of electrical equipment for mobile phones, personal computers, and automobiles.
  • the performance of Cu alloys is becoming increasingly important. Typical required characteristics are firstly high strength for light weight dangling, and secondly, high conductivity dangling for suppressing an increase in electric resistance due to a decrease in cross-sectional area due to light weight dangling. .
  • improvement of workability such as bending work accompanying downsizing of parts, improvement of heat resistance to withstand use even in relatively harsh environments, and improvement of fatigue resistance. Has become.
  • Such a high-strength and highly-conductive material is used in an environment such as an ammunition warehouse or a coal mine where excellent spark generation resistance is required in addition to the performance required for conventional tools such as wear resistance. It can also be applied to safety tool materials used below.
  • a material for example, there is an example of a Cu alloy in Patent Document 1.
  • the first method is a direct connection type continuous structure (a horizontal type, a vertical type, or the like) using a graphite mold directly connected to a holding furnace.
  • a graphite material having a self-lubricating property and a high thermal conductivity and a bulk density of 1.7 to 1.9 is generally used as a ⁇ -type material.
  • This method achieves a high V ⁇ cooling rate in the cooling process after solidification, and has a small thickness that reaches the final product without going through the subsequent solution treatment and hot working! Suitable for getting pieces! /
  • Cu is supplied through a nozzle immersed in a molten metal pool described in Patent Document 1. It is a non-direct connection type continuous structure (a vertical type, a curved type, a vertical curved type, etc.) that pours into a mold made of a metal material or an alloy material typified by a Cu alloy.
  • the nozzle thickness is limited to a relatively large one of about 100 mm or more because the nozzle is immersed in the molten metal pool in the mold. Since this method has a low cooling rate in the cooling process after solidification, a hot process such as solution treatment or hot working is indispensable until a final product is obtained.
  • an appropriate method is selected according to the required alloy composition, the piece cross-sectional shape, the cooling rate, and the like.
  • the former direct connection type
  • a large cross section size piece is used.
  • non-coupling type is often used when Cu alloy is required or when the Cu alloy contains an element that is highly reactive with C in the Dalaphite material.
  • Patent Document 1 JP-A-61-250134
  • a first object of the present invention is to provide a continuous forming mold suitable for a direct-coupled continuous forming of a Cu alloy containing an alloy element that easily reacts with C such as Zr, Ti, and Cr.
  • a second object of the present invention is to provide a continuous method for producing a Cu alloy using the mold. It should be noted that the continuous structure in the present invention has a great effect also on the continuous structure of a material other than the Cu alloy, particularly a non-ferrous metal material.
  • New aiming for higher strength and higher conductivity! / ⁇ Cu alloys contain elements that react easily with C, such as Zr, Ti, and Cr. In addition, a high cooling rate is required in the cooling process after solidification to achieve good properties. However, it was found that these alloys had the following problems caused by the reaction between C in the graphite material, which is a ⁇ -type material, and the above elements.
  • the present invention has been made to solve these problems and suppresses seizure of an initially formed solidified shell to a mold, and is sufficiently high in a cooling process after solidification!
  • the present invention relates to a continuous production mold capable of obtaining a cooling rate and a continuous production method using the same, and the invention of the following continuous production mold (1)-(5) and the continuous production method (6) — The invention of (14).
  • These inventions may be collectively referred to as the present invention.
  • a glassy carbon material, a metal-based self-lubricating composite material, or a graphite material having a bulk density of more than 1.92 is used for at least the ⁇ -shaped portion facing the solidification start position of the molten Cu alloy.
  • the continuous production type for Cu alloy is used for at least the ⁇ -shaped portion facing the solidification start position of the molten Cu alloy.
  • At least one of a graphite member a single member selected from a graphite material member, a ceramic material member, and a metal material member, or a combination of two or more members.
  • a continuous production mold for Cu alloys characterized in that the internal wall of the copper mold facing the solidification start position of the molten Cu alloy is coated with a self-lubricating material or a metal-based self-lubricating composite material.
  • a self-lubricating material member or a metal-based self-lubricating composite material member is used as an inner wall member of at least a shape corresponding to at least the solidification start position of the molten Cu alloy. , Continuous fabrication type for Cu alloy.
  • Continuous fabrication type for Cu alloy
  • a continuous manufacturing method for a Cu alloy comprising applying vibration having a component to a mold.
  • the cycle number is at least two orders of magnitude greater than the number of intermittent drawing cycles of the piece, and is perpendicular to the drawing direction.
  • a continuous production method of Cu alloy comprising: applying vibration having a component to a mold; and continuously supplying a lubricant or an anti-seizure agent between an inner wall of the mold and the piece.
  • the number of cycles is at least two orders of magnitude larger than the number of intermittent drawing cycles of the piece and is perpendicular to the drawing direction.
  • (6) The method for continuous production of a Cu alloy according to the above (6), wherein vibration having various components is applied to the mold.
  • Cu alloy force Further, in mass%, at least one of the following first group forces up to the third group: (12) The continuous production method for a Cu alloy according to the above (12), wherein one or more selected alloy components are contained in a total amount of 0.001 to 5% by mass.
  • Group 1 One or more selected from among P, B, Sb, Bi, Pb, Cd, S and As 0.001-1% by mass in total
  • Group 2 One, two or more selected from Sn, Ag, Zn, Ni, Au, Pd, Fe, W, In, and Ge 0.01-5% by mass in total
  • Group 3 One or two selected from Te, Se, Sr, Tl, Rb, Cs, Ba, Re, Os, Rh, Po, Ga, Tc, Ru, Pd, Ir, Pt and Ta Above total 0.01-3% by mass
  • the present invention it is possible to provide a continuous structure mold capable of continuously producing sound pieces efficiently and stably. Further, it is possible to provide a method for continuously producing a Cu alloy, which is excellent in properties of a final product after processing and heat treatment, for example, strength, conductivity, or fatigue strength. In particular, a great effect can be obtained when applied to the structure of a Cu alloy containing Zr, Ti, Cr, Ta, V, etc., which are elements that easily form carbides. In addition, the present invention has a great effect on materials other than Cu alloys, especially non-ferrous metal materials.
  • FIGS. 1 to 7 show an example of a direct connection type horizontal continuous structure according to the present invention.
  • the type III is directly connected to the refractory of the holding furnace wall 2 that contains the molten metal 1 of the Cu alloy.
  • a connection refractory such as a feed nozzle may be provided between the holding furnace wall and the mold.
  • a cooling chamber 1 having a structure for flowing cooling water etc. inside the mold is placed in close contact with the outside of the member 3 constituting the The heat is removed by primary cooling of the molten metal and solidification proceeds to form piece 4.
  • the piece 4 can be water jet, air jet or air-water mixed. Secondary cooling 6 is performed by joint injection and the like. The piece 4 is withdrawn in the withdrawal direction 7.
  • the mold according to the present invention includes a coating 8 on the inner wall of the mold corresponding to the solidification start position 10 of the Cu alloy melt and a mold of the mold corresponding to the Z or the Cu alloy melt upstream of the solidification start position. Some have an inner wall coating 9.
  • the ⁇ shape may include a plurality of members. That is, the ⁇ shape may be configured by the member 3 forming the ⁇ shape and the other member 3 ′ forming the ⁇ shape.
  • the inner wall surface of the mold may be deteriorated by oxidation.
  • an oxidation resistant coating such as metal plating to at least a portion corresponding to the solidification start position of the inner wall of the mold.
  • the coating material having oxidation resistance is not particularly limited, but is preferably a material which can be easily dissolved in a molten metal at the time of production and does not harm the properties of the final product.
  • the solidification start position in the present invention is defined as follows.
  • the Cu alloy that has flowed into the mold ⁇ is a molten metal upstream of the mold ⁇ , and an initial solidification shell is formed at a certain position in the mold ⁇ .
  • This solidified shell forming position is referred to as a solidification starting position.
  • the solidification start position slightly varies depending on the manufacturing conditions such as the temperature of the molten metal in the holding furnace, the mold cooling, and the drawing speed. Therefore, the solidification start position refers to the “region where solidification shell formation occurs” with a certain width in the drawing direction.
  • FIG. 1 to FIG. 7 show examples of direct connection type horizontal continuous structure type molds according to the present invention.
  • FIG. It is like rotating 90 degrees clockwise.
  • FIG. 1 shows an example of a continuous structure according to the present invention.
  • a member 3 constituting a mold including a mold portion corresponding to a solidification start position 10 of a molten Cu alloy is provided with a glassy carbon material.
  • FIG. 1 is a schematic view of a continuous structure for Cu alloy using a metal-based self-lubricating composite material or a graphite material.
  • a sound piece By using a vitreous carbon material, a metal-based self-lubricating composite material or a graphite material at least for the ⁇ -shaped portion opposite to the solidification start position of the molten Cu alloy, a sound piece can be continuously and efficiently improved. It can be manufactured stably. It is preferable to use a graphite material having a bulk density of more than 1.92.
  • the present inventors have found that, when a direct connection type continuous structure is performed by a conventional mold using a graphite material having a bulk density of 1.7 to 1.9, a large number of open pores existing on the surface of the graphite material are filled with Cu alloy. It was found that the molten metal penetrated, and the solidified shell that had initially formed was seized on the mold ⁇ , and as a result, mold ⁇ was worn due to mold eruption, and ⁇ pieces could not be pulled out. In addition, when an element that easily reacts with C such as Zr, Ti, and Cr is included, carbides are further generated at the interface between the molten metal and the mold, and the initially formed solidified shell is seized into the mold. As a result, it was found that the mold was worn due to mold shaping, and that one piece could not be pulled out.
  • the first means it is effective to use a glassy carbon material or a metal-based self-lubricating composite material from the viewpoint of the reactivity between the ⁇ -shaped material and the molten metal.
  • the glassy carbon material has a property that it is less susceptible to oxidation than the graphite material and is less likely to react with Zr, Ti, Cr and the like, and thus can sufficiently achieve the object.
  • Metal-based self-lubricating composite materials are MoS, WS, BN, and mica in a metal material matrix.
  • Such a cermet in which a self-lubricating material that hardly reacts with Cr and Zr is dispersed and mixed, and it has been found that this can sufficiently achieve the object.
  • the method for producing the composite material is not particularly limited.
  • a method in which a metal material powder and a self-lubricating material powder are mixed, compression-molded, and then sintered may be used!
  • the content of the self-lubricating material in the composite material is not particularly limited, but is preferably 10% by volume or more, more preferably 30% by volume or more, and further preferably 80% by volume or more.
  • the content of the self-lubricating material is increased, the reaction resistance and lubricity are improved, but the mechanical properties of the composite material, such as strength and thermal shock resistance, are reduced. Therefore, it is preferable to suppress the content to 85% by volume or less.
  • a metal material or an alloy material which is not particularly limited can be used. Since it is a ⁇ -shaped material in contact with the molten Cu alloy, it is preferable to use a metal material and / or an alloy material having a high melting point and high thermal conductivity. Specific examples include Cu alloys, stainless steels, Ni alloys, Co alloys, and W alloys.
  • the intermittent bow of the piece is at least two orders of magnitude larger than the number of punching cycles. Vibration having a cycle number and a component perpendicular to the drawing direction is applied to the mold, and (2) a lubricant or anti-seizing agent is continuously supplied between the inner wall and the piece of the mold. By using either one or both of them, a greater effect can be obtained. If one or both of the above measures (1) and (2) are taken, even if a graphite material having a bulk density of less than 1.92 is used as a material for forming the mold, it is possible to obtain a connection between the piece and the mold. Since seizure can be prevented, continuous production is possible.
  • the intermittent drawing method of the piece reduces the frictional resistance between the inner wall of the mold and the piece and improves the lubricity to produce a sufficiently healthy piece continuously and efficiently.
  • a vibration having a cycle number at least two orders of magnitude larger than the number of intermittent drawing cycles and a component perpendicular to the drawing direction is applied to the ⁇ type, the same effect can be obtained for a longer time.
  • the frequency is preferably 5000 cpm (83 Hz) or more, more preferably 60,000 cpm (lkHz) or more, which approaches the ultrasonic range.
  • the lubricant to be supplied between the inner wall of the ⁇ type and the ⁇ piece includes MoS, WS, BN, mica,
  • the for continuous feeding a large number of the above fine powders are lubricated with mineral oil, synthetic ester, or a mixture of them, or an anti-seizure agent is provided on the inner wall of the ⁇ type using a pressure pump. It is injected through a through hole of about 20 ⁇ m. A sufficient effect can be obtained with an injection amount of about 0.1 cc / cm 2 'min, which is about sweating. Such injection was difficult in the prior art, but was made possible by the advancement of nanotechnology, which made it easier to obtain ultrafine powders with diameters on the order of nanometers.
  • FIG. 2 is an example of a continuous structural mold according to the present invention, in which the member 3 constituting the mold is formed by one selected from a graphite material member, a ceramic material member, and a metal material member.
  • the member 3 constituting the mold is formed by one selected from a graphite material member, a ceramic material member, and a metal material member.
  • the ⁇ -shaped main body is constituted by one selected from a graphite material member, a ceramic material member, and a metal material member, and the ⁇ -shaped inner wall is coated with a self-lubricating material or a metal-based self-lubricating composite material.
  • a dense coating material composed of C, for example, a self-lubricating material such as glass is used. It is preferable to select a carbonaceous carbon material, a layered carbon material, or a diamond-like carbon material. Since the surface unevenness of the coating film substantially reflects the surface unevenness of the graphite material itself, it is desirable to select a graphite material having a bulk density as high as possible. Although not particularly limited, the bulk density is preferably 1.7 or more, more preferably 1.8 or more, and more preferably more than 1.92.
  • the ceramic material an inorganic material composed of one or more selected from oxides, nitrides, carbides, and borides is used. Although not particularly limited, from the viewpoints of mechanical strength and thermal conductivity to be provided as a ⁇ -type material, BN materials, sialon materials (Si N -A1N-A1 O-SiO phase diagram)
  • a material having low thermal conductivity it is preferable to take measures such as reducing the thickness of the mold, ie, decreasing the distance between the piece and the cooling chamber.
  • a ceramic material obtained by sintering BN and Sialon use a dense coating material composed of a nitride material, such as a self-lubricating material, in order to improve the adhesion between the mold material and the coating film. It is better to select a certain BN material.
  • the metal material a metal material or an alloy material that is not particularly limited can be used. Since it is a ⁇ -shaped material in contact with the molten Cu alloy, it is preferable to use a metal material or an alloy material having a high melting point and high thermal conductivity. Specifically, Cu alloy, stainless steel, Ni alloy, Co alloy, W alloy and the like can be mentioned. When selecting a metal material, it is better to select a metal-based dense coating material, for example, a metal-based self-lubricating composite material, in order to increase the adhesion between the mold material and the coating film.
  • a metal-based self-lubricating composite material refers to a metal material matrix containing MoS, WS, BN, and mica.
  • a cermet in which a self-lubricating material that does not easily react with Zr, Ti, Cr, etc., is dispersed and mixed. It has been found that this object can be sufficiently achieved by applying electroless plating, electroplating, or thermal spray coating to a metal material or alloy material as a ⁇ -type material. After the coating treatment, the surface of the coating film is preferably smoothed by polishing with about 1000 emery paper.
  • the content of the self-lubricating material in the composite material (cermet) to be plated or spray-coated is not particularly limited, but if the content of the self-lubricating material is increased, the reaction resistance and lubricity are improved. Approximately 10-30% by volume is preferable because the peeling resistance of the coating decreases.
  • the metal material in the composite material to be plated is not particularly limited, and a metal material or an alloy material can be used. It is preferable to use a metal material and / or an alloy material having a high melting point and a high thermal conductivity. Specific examples include Cu alloy, stainless steel, Ni alloy, Co alloy, W alloy and the like.
  • the intermittent bow I is at least two orders of magnitude larger than the number of punching cycles. Vibration having a cycle number and a component perpendicular to the drawing direction is applied to the mold, and (2) Continuous supply of lubricant or anti-seizing agent between the inner wall of the mold and the piece. ,of
  • a greater effect can be obtained by using one or both of V and shift.
  • the frictional resistance between the inner wall of the mold and the piece is reduced, and by improving the lubricity, a sufficiently sound piece can be continuously and efficiently stably obtained. Can be manufactured.
  • a vibration having a cycle number at least two orders of magnitude larger than the number of intermittent drawing cycles and a component perpendicular to the drawing direction is applied to the ⁇ type, the same effect can be obtained for a longer time.
  • the frequency is preferably 5000 cpm (83 Hz) or more, more preferably 60,000 cpm (lkHz) or more, which approaches the ultrasonic range.
  • the lubricant to be supplied between the inner wall of the ⁇ type and the ⁇ piece is as described above.
  • (C) A combination of two or more members selected from a self-lubricating material member, a metal-based self-lubricating composite material member, a graphite material member, a ceramic material member, and a metal material member ⁇ type, and at least the solidification starting position of the molten Cu alloy A continuous structure for a Cu alloy, wherein a self-lubricating material member or a metal-based self-lubricating composite material member is used for a negative inner wall member facing the device.
  • FIG. 3 is a schematic diagram of a continuous structure for Cu alloy, showing an example of the continuous structure according to the present invention.
  • the mold is composed of a plurality of member members.
  • the mold is composed of a member 3 forming the inner wall of the mold facing the solidification start position 10 of the molten Cu alloy and another member 3 ′ constituting the mold. It is configured.
  • the member 3 constituting the inner wall of the type III facing the solidification start position 10 of the molten Cu alloy is a self-lubricating material member or a metal-based self-lubricating composite material member.
  • 3 ′ one selected from a graphite material member, a ceramic material member, and a metal material member is used.
  • the type II thus constituted by a plurality of member members, that is, the type main body is made of one selected from a graphite material member, a ceramic material member and a metal material member, and
  • the inner wall member of the triangle shape is formed of a self-lubricating material member or a metal-based self-lubricating composite material member, a sound piece can be continuously and efficiently manufactured stably.
  • the graphite material member, the ceramic material member, and the metal material member used as the ⁇ -shaped main body are all as described above.
  • Any of a metal-based self-lubricating composite material in which a self-lubricating material that hardly reacts with the metal is dispersed and mixed may be selected.
  • (D) A type composed of a combination of two or more members selected from a metal-based self-lubricating composite material member, a graphite material member, a ceramic material member, and a metal material member. Characterized by being coated at least with a ⁇ -shaped inner wall 1S self-lubricating material or a metal-based self-lubricating composite material facing the solidification start position of the molten Cu alloy. , Continuous production type for Cu alloy.
  • FIG. 4 shows an example of a continuous structural mold according to the present invention, which is composed of a plurality of rectangular members, and has a self-lubricating material on the inner wall of the rectangular shape opposite to the solidification start position 10 of the molten Cu alloy.
  • FIG. 3 is a schematic view of a continuous production mold for a Cu alloy provided with a coating 8 of a metal-based self-lubricating composite material.
  • a force is selected from a metal-based self-lubricating composite material member, a graphite material member, a ceramic material member, and a metal material member. Two types of members are used.
  • the ⁇ -type upstream portion is constituted by one member selected from the group consisting of a graphite material member, a ceramic material member and a metal material member
  • the ⁇ -type downstream portion is a metal-based self-lubricating composite material member or
  • the graphite material member, the ceramic material member, the metal material member, and the metal-based self-lubricating composite material member used as the ⁇ -shaped member are all as described above.
  • the coating of the inner wall of the mold ⁇ in the matrix of self-lubricating materials such as glassy carbon material, layered carbon material, BN material, and metal material matrix contains MoS, WS, BN,
  • FIG. 5 shows another example of the continuous structure type according to the present invention.
  • the member 3 constituting the die including the die portion corresponding to the solidification start position 10 of the molten Cu alloy is formed of a metallic self-lubricating composite material.
  • Cu alloy The ceramic material is used for the purpose of suppressing the reaction with the molten metal on the inner wall of ⁇ type opposite to the molten metal Coating 9 is applied.
  • the coating method of the ceramic material may be any method such as thermal spraying or CVD.
  • FIG. 6 shows another example of the continuous structure type according to the present invention.
  • the member 3 constituting the die is formed of a metal material member, and the metal-based self-lubricating composite is formed on the inner wall of the die corresponding to the solidification start position 10 of the Cu alloy melt.
  • a coating 8 of the material is applied, and a coating 9 made of a ceramic material is applied to the inner wall of the ⁇ shape facing the molten Cu alloy in order to suppress a reaction with the molten metal.
  • the method of coating the ceramic material is the same as described above.
  • FIG. 7 shows another example of the continuous structure type according to the present invention.
  • the upstream part of the mold is constituted by the metal material member, and the downstream part of the mold is constituted by the graphite material member.
  • the inner wall of the mold is coated with a metal-based self-lubricating composite material 8 and the inner wall of the mold facing the molten copper alloy is coated with a ceramic material 9 to suppress the reaction with the molten metal. Have been.
  • the method of coating the ceramic material is the same as described above.
  • the reaction between the member and Zr, Ti, Cr, etc. in the molten metal In order to avoid this, it is more effective to coat the ceramic material on the inner wall of the ⁇ shape facing the molten Cu alloy.
  • a method of applying ceramics first coat a cushioning material with a thickness of about 50 / zm (for example, Ni plating, WC-27% by weight NiCr spraying, etc.), and cover it with a 200 m
  • a preferred method is to coat a ceramic spray with a thickness of the order of magnitude.
  • a ceramic material composed of an oxide which is more stable at a production temperature of 1250 ° C of the Cu alloy is preferred.
  • the most effective alloy system is a Cu-Ti-X system (X: Cr, Fe, Co, Ta, Nb, Mo, V, Mn, Be, Si, Ni, Sn, Ag, etc.) , Cu—Zr—X system (X: Cr, Fe, Co, Ta, Nb, Mo , V, Mn, Be, Si, Ni, Sn, Ag, etc.), Cu- ⁇ -Zr system, etc.
  • X Cr, Fe, Co, Ta, Nb, Mo , V, Mn, Be, Si, Ni, Sn, Ag, etc.
  • Cu- ⁇ -Zr system etc.
  • a great effect can be obtained when applied to other alloy systems.
  • there is a cooling process after solidification as shown by the binary phase diagram of Ti-Cr, Zr-Cr, and Ti-Zr shown in Figs. 8, 9, and 10.
  • a Ti-Cr alloy, a Zr-Cr alloy, or metal Ti, metal Zr, or metal Cr is formed.
  • These compounds and metals formed in the high-temperature region where the cooling process occurs after solidification can be solid-solved by subsequent solution treatment, as shown in the phase diagram, which tends to coarsen or agglomerate. It is almost impossible to do.
  • the piece obtained by the method of the present invention is not subjected to a hot process such as hot rolling or solution treatment as disclosed in Patent Document 1 described above, and is subjected to rolling at 600 ° C or less.
  • a hot process such as hot rolling or solution treatment as disclosed in Patent Document 1 described above
  • Combination of machining and aging between 150 ° C and 750 ° C can provide significant efficacy only after going through the process to the final product. That is, between Cu and alloying elements, such as Cu Ti and Zr Cu, or
  • the intermetallic compound between the gold elements or the fine precipitation of metal precipitates such as metal Ti, metal Zr, and metal Cr increases the strength, and thereby solidifies Ti, Zr, Cr, etc., which are harmful to electrical conductivity. It increases the conductivity by reducing the dissolved elements. If a coarse compound or a coarse precipitate exists before the aging treatment, sufficient precipitation hardening cannot be obtained. Also, the presence of these coarse particles reduces the fatigue properties ⁇ impact resistance of the final product.
  • the average cooling rate from the start of solidification to 600 ° C is preferably l ° C / s or more, more preferably 10 ° C / s or more.
  • Nb 0.01-5%
  • Ta 0.01-5%
  • Al 0.01-5%
  • Mo 0.01-5%
  • V 0.01-5%
  • Co 0.01-5%
  • Mn 0.01 Cu alloys containing one or more components selected from —5%, Si: 0.01—5%, Be: 0.01—5%, and Hf: 0.01—15%.
  • At least one group force of the following first to third groups in terms of% by mass may be used in total amount of one or more selected alloy components.
  • Group 1 Power of one, two or more selected from P, B, Sb, Bi, Pb, Cd, S and As 0.001-1% by mass
  • Group 2 One, two or more selected from Sn, Ag, Zn, Ni, Au, Pd, Fe, W, In, and Ge 0.01-5% by mass in total
  • Group 3 One or two selected from Te, Se, Sr, Tl, Rb, Cs, Ba, Re, Os, Rh, Po, Ga, Tc, Ru, Pd, Ir, Pt and Ta Above total 0.01-3% by mass
  • a Cu alloy containing, by mass%, one or more alloy components selected from among Li, Ca, Mg and rare earth elements in a total amount of 0.001-2 mass%.
  • the rare earth elements mean Sc, Y, and lanthanoids, and the raw material of each element may be added to the raw material, or may be added to misch metal.
  • a predetermined Cu alloy Prior to the continuous structure using the mold in the method of the present invention, a predetermined Cu alloy is melted.
  • a molten metal having a predetermined chemical composition is formed in a melting furnace lined with a graphite material or the like. It is desirable to perform the dissolving atmosphere in a non-oxidizing atmosphere. When it is necessary to dissolve in the atmosphere, it is effective to use a flux (eg cryolite, fluorite, etc.) or charcoal powder to block the atmosphere.
  • a flux eg cryolite, fluorite, etc.
  • any type such as a horizontal type and a vertical type may be used as long as it is a direct connection type continuous structure in which a holding furnace and a mold are directly connected.
  • the type III according to the present invention has low reactivity with molten metal and good lubricity, there are few operational problems when producing the Cu alloy of the present invention.
  • the inner wall of the mold near the solidification start position gradually decreases in thickness due to reaction with the molten metal and wear, so that the piece may be hardly pulled out by the pulling force of the piece. In such a case, it is effective to uniformly reduce the thickness by moving the solidification position by adjusting the cooling conditions of the mold, the drawing speed, and the like.
  • the piece is intermittently pulled out.
  • Either a pull-out stop-push-back pattern or (D) a pull-stop-push-back stop-out pattern can be used.
  • cooling during the cooling process after solidification A higher rejection speed is desirable.
  • water injection, air injection, or air-water mixture injection immediately after leaving the mold is effective, but of course, other methods may be used.
  • Cu alloy containing 2.0 ⁇ 0.1wt% Ti, 1.0 ⁇ 0.1wt% Cr, 0.4 ⁇ 0.02wt% Sn, 0.1 ⁇ 0.01wt% Zn is melted in a high-frequency vacuum melting furnace, and various productions shown in Tables 1 and 2 are performed. Continuous production tests were performed by the method (37 types). The melted Cu alloy melt was transferred to a holding furnace and kept at 1250 ° C., and a piece having a cross section of 20 mm ⁇ 200 mm was intermittently extracted under predetermined conditions. Refractories such as melting furnaces or holding furnaces were each made of graphite. The atmosphere during the pouring was air shut off by the Ar gas flow.
  • a water-cooled cooling chamber made of a Cu alloy was placed on the outside of the mold and the primary cooling was performed, and the piece leaving the mold was subjected to secondary cooling by air-water mixed injection.
  • the temperature was basically measured by using a thermocouple or a radiation thermometer after exiting the ⁇ type.
  • a through hole was drilled to a position 5 mm outside of the inner wall of the mold and the thermocouple was inserted to measure the mold temperature, and the heat transfer calculation was performed using the physical properties of each mold material.
  • the coagulation start position was estimated. From the above data, the average cooling rate from the start of solidification to 600 ° C was calculated. In the tests shown in Tables 1 and 2, the cooling rate was controlled within the range of 5 ⁇ 2 ° C.
  • Example A In exactly the same way as in Example A, a Cu alloy (34 types) having the composition shown in Table 3 was melted and subjected to continuous production tests under different manufacturing conditions, and evaluated in exactly the same manner as in Example A. did. Tables 4 and 5 show the results. In the method of the present invention, good results were obtained for any type, any manufacturing condition, and any chemical composition. On the other hand, in the comparative example in which the type ⁇ was changed, the quality was satisfactory and the result was not obtained.
  • the cooled pieces are cold rolled to 3 mm, then aged at 400 ° C for 2 hours in an inert gas atmosphere, cold rolled to 0.5 mm again, and finally aged at 350 ° C for 6 hours Processed.
  • the conductivity of the obtained test material and the tensile strength by a tensile test were evaluated by the following methods.
  • a test piece having a width of 10 mm and a length of 60 mm was sampled from the above test material, and a current was passed in the longitudinal direction of the test piece to measure a potential difference between both ends of the test piece, and an electric resistance was obtained by a four-terminal method. Subsequently, the electrical resistance (resistivity) per unit volume was calculated from the volume of the test piece measured with a micrometer, and the specific force with the resistivity of the standard sample annealed with polycrystalline pure copper, 1.72 ⁇ cm, was also determined by the conductivity [IACS ( %;)].
  • the cooling rate is lower than 0.5 ° C / s, which is the comparative method, cracks occur during cold rolling, and even if cold rolling is performed, the balance between strength and conductivity is poor.
  • the method of the present invention has a good balance between the two, and has a high tensile strength in relation to the electrical conductivity.
  • IACS means the percentage with respect to the electrical conductivity of the pure copper polycrystalline material.
  • Table 7 shows the results of the same evaluation of the properties of the alloys shown in Table 3 under the above manufacturing conditions, with the cooling rate from the start of solidification to 600 ° C being 5 ° C / s. As a result, all the alloys had a balance between strength and electrical conductivity satisfying the above equation (1), and good results were obtained by the present invention.
  • the present invention relates to a continuous structure used mainly for a direct connection type continuous structure in which a holding furnace is directly connected to a mold, and a method for continuously manufacturing a Cu alloy using the continuous structure. That is, the present invention provides a mold capable of continuously and efficiently producing a healthy piece, and furthermore, has properties, such as strength and conductivity, or impact resistance, of a final product after processing and heat treatment. It provides a continuous production method for Cu alloys with excellent fatigue strength, and is particularly susceptible to carbide formation./ For the production of Cu alloys containing the elements Zr, Ti, Cr, Ta, V, etc. Big effect when applied can get.
  • FIG. 1 is an example of a continuous fabrication type according to the present invention.
  • FIG. 2 is an example of a continuous molding type according to the present invention, in which a coating 8 of a self-lubricating material or a metal-based self-lubricating composite material is applied to an inner wall of the type III, which is opposed to a solidification start position of a molten Cu alloy. ing.
  • FIG. 3 is an example of a continuous forming machine for Cu alloy according to the present invention, which uses a die formed of a plurality of member members.
  • FIG. 4 is an example of a continuous molding die according to the present invention, which is constituted by a plurality of die members and has a self-lubricating material or metal on an inner wall of the die which is opposed to a solidification start position of a molten Cu alloy.
  • FIG. 1 is a schematic view of a continuous production mold for a Cu alloy provided with a coating 8 of a self-lubricating composite material.
  • FIG. 5 shows another example of the continuous fabrication type according to the present invention.
  • a coating 9 made of a ceramic material is applied to the inner wall of the rectangular shape opposite to the molten Cu alloy for the purpose of suppressing the reaction with the molten metal.
  • FIG. 6 shows another example of the continuous structure type according to the present invention.
  • a metal-based self-lubricating composite material coating 8 is applied to the inner wall of the ⁇ type opposite to the solidification start position of the molten Cu alloy, and the purpose is to suppress the reaction with the molten metal on the inner wall of the ⁇ ⁇ type facing the molten Cu alloy.
  • a coating 9 of a ceramic material is applied.
  • FIG. 7 shows another example of the continuous fabrication type according to the present invention.
  • the metal material member constitutes the upstream part of the mold, and the graphite material member constitutes the downstream part of the mold.
  • the metal-based self-lubrication is applied to the inner wall of the mold, which is opposite to the solidification start position of the molten Cu alloy.
  • a coating 8 of a conductive composite material is applied, and a coating 9 made of a ceramic material is applied to the inner wall of the ⁇ shape facing the molten Cu alloy for the purpose of suppressing the reaction with the molten metal.
  • FIG. 8 is a state diagram of a Ti—Cr alloy.
  • FIG. 9 is a state diagram of a Zr—Cr alloy.
  • FIG. 10 is a state diagram of a TVZr alloy.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Continuous Casting (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)

Abstract

Cette invention concerne un moule de coulage en continu pour alliage de cuivre, caractérisé en ce que un matériau vitreux au carbone, un matériau composite autolubrifiant métallique ou un matériau graphité d'une densité apparente de plus 1,92 est utilisé sur au moins une partie du moule opposée au point de départ de solidification de l'alliage de cuivre en fusion ; ou un moule de coulage en continu pour alliage de cuivre caractérisé en ce qu'au moins la paroi intérieure du moule opposée au point de départ de solidification de l'alliage de cuivre en fusion est enduite d'un matériau autolubrifiant ou d'un matériau composite autolubrifiant métallique. L'invention concerne également un procédé de coulage en continu d'alliage de cuivre caractérisé par le coulage en continu dans le moule susdécrit selon la méthode d'étirage intermittent des brames, avec une vibration dont la fréquence dépasse d'au moins deux chiffres la fréquence d'étirage intermittent des brames, vibration possédant une composante perpendiculaire à la direction d'étirage, qui est appliquée au moule, ou bien un procédé selon lequel un lubrifiant ou un antigrippant est introduit en continu dans l'espace compris entre le moule et toute coquille solidifiée.
PCT/JP2004/013756 2003-09-24 2004-09-21 Moule de coulage et procede de coulage en continu pour alliage de cuivre Ceased WO2005028143A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
JP2005514086A JP4333881B2 (ja) 2003-09-24 2004-09-21 連続鋳造鋳型及び銅合金の連続鋳造方法
EP04787939A EP1688198A4 (fr) 2003-09-24 2004-09-21 Moule de coulage et procede de coulage en continu pour alliage de cuivre

Applications Claiming Priority (6)

Application Number Priority Date Filing Date Title
JP2003331909 2003-09-24
JP2003-331909 2003-09-24
JP2004097223 2004-03-29
JP2004-097223 2004-03-29
JP2004234641 2004-08-11
JP2004-234641 2004-08-11

Publications (1)

Publication Number Publication Date
WO2005028143A1 true WO2005028143A1 (fr) 2005-03-31

Family

ID=34381782

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2004/013756 Ceased WO2005028143A1 (fr) 2003-09-24 2004-09-21 Moule de coulage et procede de coulage en continu pour alliage de cuivre

Country Status (5)

Country Link
US (1) US20060180293A1 (fr)
EP (1) EP1688198A4 (fr)
JP (1) JP4333881B2 (fr)
TW (1) TWI272145B (fr)
WO (1) WO2005028143A1 (fr)

Cited By (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102006015282A1 (de) * 2006-04-01 2007-10-04 Honeywell Technologies Sarl Ecc Kokille und Verfahren zum Gießen von Rotguss
JP2009242882A (ja) * 2008-03-31 2009-10-22 Nippon Mining & Metals Co Ltd 精密プレス加工に適したチタン銅
JP2011036903A (ja) * 2009-08-18 2011-02-24 Materials Solution Inc 銅合金の製造方法
CN102476177A (zh) * 2010-11-29 2012-05-30 株洲南方有色焊材有限公司 一种铜合金线坯上引法
CN103695697A (zh) * 2013-12-03 2014-04-02 江苏帕齐尼铜业有限公司 一种铜铬合金及其制备方法
JP2014095107A (ja) * 2012-11-07 2014-05-22 Fujikura Ltd Ｃｕ−Ｍｇ合金体、Ｃｕ−Ｍｇ合金体の製造方法および伸線材
CN104051076A (zh) * 2014-06-05 2014-09-17 锐展(铜陵)科技有限公司 一种汽车电线电缆用低膨胀铜合金线的制备方法
CN104046837A (zh) * 2014-06-05 2014-09-17 锐展(铜陵)科技有限公司 一种汽车工业用无铅铜合金线的制备方法
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
CN104046838A (zh) * 2014-06-05 2014-09-17 锐展(铜陵)科技有限公司 一种汽车线缆用高强韧铜合金线的制备方法
CN104152728A (zh) * 2014-06-05 2014-11-19 锐展(铜陵)科技有限公司 一种汽车线束用高导热铜合金线的制备方法
KR20180125449A (ko) * 2016-03-30 2018-11-23 미쓰비시 마테리알 가부시키가이샤 전자·전기 기기용 구리 합금, 전자·전기 기기용 구리 합금판 조재, 전자·전기 기기용 부품, 단자, 버스바, 및 릴레이용 가동편
US11104977B2 (en) 2018-03-30 2021-08-31 Mitsubishi Materials Corporation Copper alloy for electronic/electric device, copper alloy sheet/strip material for electronic/electric device, component for electronic/electric device, terminal, and busbar
US11203806B2 (en) 2016-03-30 2021-12-21 Mitsubishi Materials Corporation Copper alloy for electronic and electrical equipment, copper alloy plate strip for electronic and electrical equipment, component for electronic and electrical equipment, terminal, busbar, and movable piece for relay
US11319615B2 (en) 2016-03-30 2022-05-03 Mitsubishi Materials Corporation Copper alloy for electronic and electrical equipment, copper alloy plate strip for electronic and electrical equipment, component for electronic and electrical equipment, terminal, busbar, and movable piece for relay
US11655523B2 (en) 2018-03-30 2023-05-23 Mitsubishi Materials Corporation Copper alloy for electronic/electric device, copper alloy sheet/strip material for electronic/electric device, component for electronic/electric device, terminal, and busbar

Families Citing this family (38)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
ATE539823T1 (de) * 2008-03-05 2012-01-15 Southwire Co Ultraschallsonde mit schutzschicht aus niobium
RU2510420C2 (ru) * 2009-09-07 2014-03-27 Сирогане Ко., Лтд. Медный сплав и способ получения медного сплава
US8652397B2 (en) 2010-04-09 2014-02-18 Southwire Company Ultrasonic device with integrated gas delivery system
SI2556176T1 (sl) 2010-04-09 2021-01-29 Southwire Company, Llc Ultrazvočno razplinjevanje staljenih kovin
CN102634688B (zh) * 2011-02-10 2014-05-07 湖南特力新材料有限公司 一种无铅易切削铜合金及制备方法
JP5802150B2 (ja) * 2012-02-24 2015-10-28 株式会社神戸製鋼所 銅合金
CN103114218B (zh) * 2013-03-11 2014-07-16 武汉大学 一种铜铬合金的制备方法
CN103114222B (zh) * 2013-03-14 2014-10-22 上海天申铜业集团有限公司 一种无铅水表表壳的铸造方法
KR102306057B1 (ko) 2013-11-18 2021-09-29 사우쓰와이어 컴퍼니, 엘엘씨 용융 금속의 가스 제거를 위한 가스 출구를 갖는 초음파 탐침
CN104046831A (zh) * 2014-06-05 2014-09-17 锐展(铜陵)科技有限公司 一种汽车用铜合金电线的制备方法
CN104046832A (zh) * 2014-06-05 2014-09-17 锐展(铜陵)科技有限公司 一种汽车发电机用高导电铜合金线的制备方法
JP6488951B2 (ja) * 2014-09-25 2019-03-27 三菱マテリアル株式会社 鋳造用モールド材及びＣｕ−Ｃｒ−Ｚｒ合金素材
CN104588618B (zh) * 2014-11-28 2017-01-18 太原科技大学 一种镁合金复合板连铸装置
CN104475468B (zh) * 2014-12-09 2016-08-24 中色（天津）特种材料有限公司 N6镍合金线材连铸连拔加工工艺
JP6228941B2 (ja) * 2015-01-09 2017-11-08 Ｊｘ金属株式会社 めっき層を有するチタン銅
CN104630546A (zh) * 2015-03-05 2015-05-20 苏州市凯业金属制品有限公司 一种高强耐热铜合金金属管
CN104928528A (zh) * 2015-07-06 2015-09-23 苏州科茂电子材料科技有限公司 一种导电铜合金材料及其制备方法
CN104928523A (zh) * 2015-07-10 2015-09-23 苏州科茂电子材料科技有限公司 一种通信电缆用铜合金导线材料及其制备方法
US10233515B1 (en) 2015-08-14 2019-03-19 Southwire Company, Llc Metal treatment station for use with ultrasonic degassing system
CN105108079A (zh) * 2015-09-24 2015-12-02 云南新铜人实业有限公司 一种水平连铸铜板带生产工艺
CN106111931B (zh) * 2016-06-28 2018-06-05 北京科技大学 一种金属包覆材料固/液连铸复合成形设备与工艺方法
CN106424613A (zh) * 2016-11-29 2017-02-22 郑州中拓知识产权代理有限公司 一种铜棒连铸机
KR101830841B1 (ko) 2016-11-29 2018-02-22 한국생산기술연구원 고내마모성을 갖는 싱크로나이저 링용 동합금 및 이의 제조방법
CN106735003B (zh) * 2016-12-08 2018-09-28 北京科技大学 一种高强高导Cu-Cr-Zr合金棒材的非真空熔炼水平连铸生产工艺
CN106583672B (zh) * 2016-12-09 2018-09-25 北京科技大学 一种铜铬系合金水平连铸工艺
CN107511469A (zh) * 2017-10-13 2017-12-26 安阳恒安电机有限公司 一种电机转子鼠笼低压铸铜设备、铸铜及其铸铜方法
CN110396621B (zh) * 2019-08-27 2020-12-08 天长市华海电子科技有限公司 一种抗晶间腐蚀锻造件及其制备方法
CN113458352B (zh) 2020-03-30 2023-11-24 日本碍子株式会社 Cu-Ni-Sn合金的制造方法及用于其的冷却器
CN111850345B (zh) * 2020-07-23 2021-06-18 唐山中科量子激光科技有限公司 一种耐磨抗高温侵蚀合金材料、结晶器铜板表面处理方法及结晶器铜板
CN112355263A (zh) * 2020-10-14 2021-02-12 刘珍 一种用于铝合金加工的半固态成形装置
JP7433263B2 (ja) * 2021-03-03 2024-02-19 日本碍子株式会社 Ｃｕ－Ｎｉ－Ｓｎ合金の製造方法
JP7735699B2 (ja) * 2021-07-13 2025-09-09 株式会社レゾナック 水平連続鋳造装置、アルミニウム合金鋳造棒の製造方法
CN113680980B (zh) * 2021-09-06 2022-12-09 西安斯瑞先进铜合金科技有限公司 一种采用水平连铸铜锰合金的生产工艺
CN114012052B (zh) * 2021-12-30 2022-05-03 东北大学 一种铝合金铸锭水平连铸设备
CN115475830A (zh) * 2022-09-14 2022-12-16 南京航空航天大学 一种高温合金管材的短流程制备加工方法
CN115786752B (zh) * 2022-11-24 2024-05-31 有研工程技术研究院有限公司 一种提高白铜合金管材耐蚀性能的方法
CN116117084B (zh) * 2022-12-16 2025-01-21 攀钢集团攀枝花钢铁研究院有限公司 一种高强高韧冷作模具钢坯的制备方法
CN115852201A (zh) * 2022-12-28 2023-03-28 北冶功能材料(江苏)有限公司 一种铜镍锡合金铸锭的生产方法

Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS58123862A (ja) * 1982-01-20 1983-07-23 Nippon Mining Co Ltd 半導体機器のリ−ド材用銅合金の製造方法
JPS61169149A (ja) * 1985-01-22 1986-07-30 Nippon Mining Co Ltd 連続鋳造方法
JPH03155436A (ja) * 1989-11-10 1991-07-03 Sumitomo Light Metal Ind Ltd 水平連続鋳造方法
JPH03210942A (ja) * 1990-01-11 1991-09-13 Sumitomo Metal Ind Ltd 鋼の連続鋳造方法
JPH04266457A (ja) * 1991-02-22 1992-09-22 Hitachi Cable Ltd 連続鋳造用鋳型
JPH05318034A (ja) * 1992-05-22 1993-12-03 Furukawa Electric Co Ltd:The 連続鋳造用複合黒鉛鋳型
JPH06179930A (ja) * 1992-08-25 1994-06-28 Tatsuta Electric Wire & Cable Co Ltd 黒鉛製るつぼ又は鋳型
JPH09141394A (ja) * 1995-11-17 1997-06-03 Sumitomo Metal Ind Ltd 連続鋳造用鋳型およびその製造方法と使用方法
JPH11147162A (ja) * 1997-11-13 1999-06-02 Tokai Carbon Co Ltd 連続鋳造用黒鉛鋳型

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3424228A (en) * 1966-04-08 1969-01-28 Ducommun Inc Anisotropic mold liner for continuous casting of metals
US3435881A (en) * 1967-01-03 1969-04-01 Carbone Corp Anisotropic continuous casting mold
DE2634633C2 (de) * 1976-07-31 1984-07-05 Kabel- und Metallwerke Gutehoffnungshütte AG, 3000 Hannover Stranggießkokille aus einem Kupferwerkstoff, insbesondere zum Stranggießen von Stahl
DE2657207C2 (de) * 1976-12-17 1978-10-05 Kreidler Werke Gmbh, 7000 Stuttgart Verfahren zum Stranggießen von Metall-Legierungen, insbesondere Messing-Legierungen und Stranggießkokille zur Durchführung des Verfahrens
JPS5785652A (en) * 1980-11-19 1982-05-28 Kawasaki Steel Corp Continuous casting method for hollow blank material for pipe making
JPS59133942A (ja) * 1983-01-21 1984-08-01 Kobe Steel Ltd 水平連続鋳造用鋳型の内面処理方法
US5171491A (en) * 1986-02-04 1992-12-15 The Carborundum Company Method of producing near net shape fused cast refractories
JPH026037A (ja) * 1988-06-27 1990-01-10 Nkk Corp 鋼の連続鋳造方法
CH695210A5 (de) * 2000-12-11 2006-01-31 Concast Ag Kokille zum Stranggiessen einer Stahlschmelze.

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS58123862A (ja) * 1982-01-20 1983-07-23 Nippon Mining Co Ltd 半導体機器のリ−ド材用銅合金の製造方法
JPS61169149A (ja) * 1985-01-22 1986-07-30 Nippon Mining Co Ltd 連続鋳造方法
JPH03155436A (ja) * 1989-11-10 1991-07-03 Sumitomo Light Metal Ind Ltd 水平連続鋳造方法
JPH03210942A (ja) * 1990-01-11 1991-09-13 Sumitomo Metal Ind Ltd 鋼の連続鋳造方法
JPH04266457A (ja) * 1991-02-22 1992-09-22 Hitachi Cable Ltd 連続鋳造用鋳型
JPH05318034A (ja) * 1992-05-22 1993-12-03 Furukawa Electric Co Ltd:The 連続鋳造用複合黒鉛鋳型
JPH06179930A (ja) * 1992-08-25 1994-06-28 Tatsuta Electric Wire & Cable Co Ltd 黒鉛製るつぼ又は鋳型
JPH09141394A (ja) * 1995-11-17 1997-06-03 Sumitomo Metal Ind Ltd 連続鋳造用鋳型およびその製造方法と使用方法
JPH11147162A (ja) * 1997-11-13 1999-06-02 Tokai Carbon Co Ltd 連続鋳造用黒鉛鋳型

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP1688198A4 *

Cited By (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102006015282A1 (de) * 2006-04-01 2007-10-04 Honeywell Technologies Sarl Ecc Kokille und Verfahren zum Gießen von Rotguss
JP2009242882A (ja) * 2008-03-31 2009-10-22 Nippon Mining & Metals Co Ltd 精密プレス加工に適したチタン銅
JP2011036903A (ja) * 2009-08-18 2011-02-24 Materials Solution Inc 銅合金の製造方法
CN102476177A (zh) * 2010-11-29 2012-05-30 株洲南方有色焊材有限公司 一种铜合金线坯上引法
CN102476177B (zh) * 2010-11-29 2013-05-29 株洲南方有色焊材有限公司 一种铜合金线坯上引法
JP2014095107A (ja) * 2012-11-07 2014-05-22 Fujikura Ltd Ｃｕ−Ｍｇ合金体、Ｃｕ−Ｍｇ合金体の製造方法および伸線材
CN103695697B (zh) * 2013-12-03 2016-04-20 江苏帕齐尼铜业有限公司 一种铜铬合金及其制备方法
CN103695697A (zh) * 2013-12-03 2014-04-02 江苏帕齐尼铜业有限公司 一种铜铬合金及其制备方法
CN104051076A (zh) * 2014-06-05 2014-09-17 锐展(铜陵)科技有限公司 一种汽车电线电缆用低膨胀铜合金线的制备方法
CN104046837A (zh) * 2014-06-05 2014-09-17 锐展(铜陵)科技有限公司 一种汽车工业用无铅铜合金线的制备方法
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
CN104046838A (zh) * 2014-06-05 2014-09-17 锐展(铜陵)科技有限公司 一种汽车线缆用高强韧铜合金线的制备方法
CN104152728A (zh) * 2014-06-05 2014-11-19 锐展(铜陵)科技有限公司 一种汽车线束用高导热铜合金线的制备方法
KR20180125449A (ko) * 2016-03-30 2018-11-23 미쓰비시 마테리알 가부시키가이샤 전자·전기 기기용 구리 합금, 전자·전기 기기용 구리 합금판 조재, 전자·전기 기기용 부품, 단자, 버스바, 및 릴레이용 가동편
KR102296652B1 (ko) 2016-03-30 2021-08-31 미쓰비시 마테리알 가부시키가이샤 전자·전기 기기용 구리 합금, 전자·전기 기기용 구리 합금판 조재, 전자·전기 기기용 부품, 단자, 버스바, 및 릴레이용 가동편
US11203806B2 (en) 2016-03-30 2021-12-21 Mitsubishi Materials Corporation Copper alloy for electronic and electrical equipment, copper alloy plate strip for electronic and electrical equipment, component for electronic and electrical equipment, terminal, busbar, and movable piece for relay
US11319615B2 (en) 2016-03-30 2022-05-03 Mitsubishi Materials Corporation Copper alloy for electronic and electrical equipment, copper alloy plate strip for electronic and electrical equipment, component for electronic and electrical equipment, terminal, busbar, and movable piece for relay
US11104977B2 (en) 2018-03-30 2021-08-31 Mitsubishi Materials Corporation Copper alloy for electronic/electric device, copper alloy sheet/strip material for electronic/electric device, component for electronic/electric device, terminal, and busbar
US11655523B2 (en) 2018-03-30 2023-05-23 Mitsubishi Materials Corporation Copper alloy for electronic/electric device, copper alloy sheet/strip material for electronic/electric device, component for electronic/electric device, terminal, and busbar

Also Published As

Publication number Publication date
US20060180293A1 (en) 2006-08-17
JP4333881B2 (ja) 2009-09-16
TW200528213A (en) 2005-09-01
TWI272145B (en) 2007-02-01
EP1688198A4 (fr) 2007-03-21
JPWO2005028143A1 (ja) 2007-11-15
EP1688198A1 (fr) 2006-08-09

Similar Documents

Publication Publication Date Title
WO2005028143A1 (fr) Moule de coulage et procede de coulage en continu pour alliage de cuivre
TW457154B (en) Electrode for surface treatment by electric discharge, process for making the same, method and apparatus for surface treatment by electric discharge
JP2002503764A (ja) アルミニド粉末の熱機械的加工によるアルミニドシートの製造方法
WO2004070070A1 (fr) Alliage de cu et son procede de production
WO2006109801A1 (fr) Alliage de cuivre et procédé servant à produire celui-ci
Huang et al. Effects of TiN nanoparticles on the microstructure and properties of W–30Cu composites prepared via electroless plating and powder metallurgy
Luo et al. The activated sintering of WCu composites through spark plasma sintering
JPWO2005072891A1 (ja) 銅合金の連続鋳造方法
Kumar et al. Coatings on reinforcements in aluminum metal matrix composites
EP1594644B1 (fr) Formation d'alliages metalliques servant de barrieres thermiques
CN102686337B (zh) 含活性元素的铜合金线材的制造方法
Rominiyi et al. Spark plasma sintering of discontinuously reinforced titanium matrix composites: densification, microstructure and mechanical properties—a review
TW576767B (en) Ingot-mold wall, especially a broad side wall of a continuous casting mold for steel
CN101574761B (zh) 用于高温热电偶保护管表面熔覆的粉心焊丝及制备方法
CN112877600B (zh) 一种电子电力用铜钢固液复合双金属材料及其制备方法
WO2012164581A2 (fr) Procédé de production de composites à matrice métal-aluminium renforcés
JP2007016288A (ja) 軸受材被覆摺動部材の製造方法及び軸受材被覆摺動部材
Tsyganov et al. Steel-copper nano composited materials
Kaya Ceramic reinforced composite coatings on cold work tool steel fabricated by wired direct energy deposited plasma
KR100740899B1 (ko) 강 연속 주조 주형의 주형 벽, 특히 넓은 쪽 벽
Cao et al. Mechanical properties of iron matrix composites reinforced by copper-coated hybrid ceramic particles
JPS616242A (ja) 繊維強化金属複合材料
US3764308A (en) Multi phase strip from particle and powder mixture
US3819311A (en) Apparatus for forming multi-phase strip from particle and powder mixture
KR19990080858A (ko) 전극 재료, 전극 재료의 제조 방법 및 전극의 제조 방법

Legal Events

Date Code Title Description
AK Designated states

Kind code of ref document: A1

Designated state(s): AE AG AL AM AT AU AZ BA BB BG BW BY BZ CA CH CN CO CR CU CZ DK DM DZ EC EE EG ES FI GB GD GE GM HR HU ID IL IN IS JP KE KG KP KZ LC LK LR LS LT LU LV MA MD MK MN MW MX MZ NA NI NO NZ PG PH PL PT RO RU SC SD SE SG SK SY TJ TM TN TR TT TZ UA UG US UZ VN YU ZA ZM

AL Designated countries for regional patents

Kind code of ref document: A1

Designated state(s): BW GH GM KE LS MW MZ NA SD SZ TZ UG ZM ZW AM AZ BY KG MD RU TJ TM AT BE BG CH CY DE DK EE ES FI FR GB GR HU IE IT MC NL PL PT RO SE SI SK TR BF CF CG CI CM GA GN GQ GW ML MR SN TD TG

121 Ep: the epo has been informed by wipo that ep was designated in this application
WWE Wipo information: entry into national phase

Ref document number: 2006103368

Country of ref document: RU

WWE Wipo information: entry into national phase

Ref document number: 2005514086

Country of ref document: JP

WWE Wipo information: entry into national phase

Ref document number: 2004787939

Country of ref document: EP

WWE Wipo information: entry into national phase

Ref document number: 11386924

Country of ref document: US

DPEN Request for preliminary examination filed prior to expiration of 19th month from priority date (pct application filed from 20040101)
WWP Wipo information: published in national office

Ref document number: 2004787939

Country of ref document: EP

WWW Wipo information: withdrawn in national office

Ref document number: 2004787939

Country of ref document: EP