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US20060180293A1 - Continuous casting mold and a continuous casting method of copper alloy - Google Patents

Continuous casting mold and a continuous casting method of copper alloy Download PDF

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Publication number
US20060180293A1
US20060180293A1 US11/386,924 US38692406A US2006180293A1 US 20060180293 A1 US20060180293 A1 US 20060180293A1 US 38692406 A US38692406 A US 38692406A US 2006180293 A1 US2006180293 A1 US 2006180293A1
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United States
Prior art keywords
alloy
mold
continuous casting
metal
wall
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Abandoned
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US11/386,924
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English (en)
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.)
SUMOTOMO METAL INDUSTRIES Ltd
Nippon Steel Corp
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Sumitomo Metal Industries Ltd
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Assigned to SUMOTOMO METAL INDUSTRIES, LTD. reassignment SUMOTOMO METAL INDUSTRIES, LTD. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: AOKI, MASAHIRO, YOSHIDA, NAOTSUGU, YONEMURA, MITSUHARU, MAEHARA, YASUHIRO, NAKAJIMA, KEIJI
Publication of US20060180293A1 publication Critical patent/US20060180293A1/en
Abandoned legal-status Critical Current

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    • 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 casting mold and a continuous casting method of a Cu alloy, particularly, a casting mold used for a direct-connection type of continuous casting machine, in which a mold is directly connected to a holding furnace, and a continuous casting method of a Cu alloy using this mold.
  • the typical first necessary characteristic is higher strength for a reduction in weight
  • the second is higher electric conductivity for suppressing a rise of electric resistance caused by reduction in the sectional area due to the reduction in weight.
  • the improvement in workability such as bending workability due to the downsizing of parts, the improvement in heat resistance in order to ensure usability even in relatively severe environments, and the improvement in fatigue strength are also important problems.
  • Such a highly strong and highly electric-conductive material can also be applied to safety tool materials used in an environment such as an ammunition chamber or a coal mine which needs excellent spark generation resistance, in addition to the wear resistance needed for conventional tools.
  • a material is exemplified the Cu alloy disclosed in the Patent Document 1 below.
  • the first method is a direct-connection type of continuous casting including horizontal type and vertical type casting, using a graphite-made mold directly connected to a holding furnace. Since a supply of a lubricant is extremely difficult in the direct-connection type of continuous casting, graphite with a bulk density of 1.7 to 1.9, which has a self-lubricating property and high heat conductivity, has widely been used for the mold material. This method is suitable for obtaining a slab or a bloom with relatively small sectional area. In such type of continuous casting process, the cooling rate after solidification is relatively high, leading to a high performance of a final product even without a subsequent hot process such as a solution treatment or a hot working.
  • the second method is a non-direct-connection type of continuous casting including vertical type, curved type and vertical-curved type casting, described in the Patent Document 1, in which melt is poured into a mold made of a metal such as Cu or an alloy such as a Cu alloy through a nozzle immersed into a melt pool.
  • the slabs to be cast are limited to a relatively large size with a thickness of about 100 mm or more, since the nozzle can be immersed into the melt pool within the mold.
  • This method essentially requires a hot process such as a solution treatment or a hot working in the later production process because of a low cooling rate in the cooling process after solidification.
  • a proper method is selected from these two kinds of continuous casting methods according to the required alloy composition, slab sectional shape, cooling rate, or the like.
  • the former direct connection type is adapted when a high cooling rate is needed or when the Cu alloy is free from highly reactive elements with C in the graphite.
  • the latter non-direct connection type is adapted when a slab of a large sectional size is needed or when the Cu alloy contains highly reactive elements with C in the graphite.
  • Patent Document Japanese Patent Unexamined Publication No. S61-250134.
  • the primary objective of the present invention is to provide a continuous casting mold suitable for a direct-connection type of continuous casting of the Cu alloy containing elements such as Zr, Ti, and Cr that are reactive with C.
  • the second objective of the present invention is to provide a continuous casting method of the Cu alloy using the above-described mold.
  • the continuous casting mold of the present invention is highly effective for continuous casting not only of Cu alloys but also of such materials as non-ferrous metals other than Cu alloys.
  • new Cu alloys intended for higher strength and higher electric conductivity contain elements such as Zr, Ti and Cr, which easily react with C. They also need a high cooling rate in the cooling process after solidification in order to attain satisfactory characteristics of the final products.
  • these alloys are found to have the following problems, which results from the reaction of above-mentioned elements with C in the graphite mold.
  • the present invention relates to a continuous casting mold, capable of providing a sufficiently high cooling rate in the cooling process after solidification, while suppressing the sticking of the initially formed solidification shell to the mold, and a continuous casting method using the mold, and involves the following inventions of continuous casting molds (1) to (5) and inventions of continuous casting methods (6) to (12). These inventions are hereinafter referred to as the present inventions (1) to (12), respectively, or often are referred to collectively as the present invention.
  • a continuous casting mold for a Cu alloy using any one member selected from a glassy carbon or a metal-based self-lubricating composite, at least for the mold member including the solidification starting position of the Cu alloy melt.
  • a continuous casting mold for a Cu alloy composed of any one member selected from a graphite, a ceramic and a metal member or of a combination of two or more parts of members thereof, in which at least the inner wall in the solidification starting position of the Cu alloy melt is coated with a self-lubricant or a metal-based self-lubricating composite material.
  • a continuous casting mold for a Cu alloy composed of a combination of two or more parts of members selected from a self-lubricant, a metal-based self-lubricating composite, a graphite, a ceramic and a metal member, in which the self-lubricant or the metal-based self-lubricating composite member is used at least for the inner wall in the solidification starting position of the Cu alloy melt.
  • a continuous casting mold for a Cu alloy composed of a combination of two or more parts of members selected from a self-lubricant, a metal-based self-lubricating composite, a graphite, a ceramic and a metal member, in which at least the inner wall in the solidification starting position of the Cu alloy melt is coated with a self-lubricant or a metal-based self-lubricating composite material.
  • a continuous casting method of a Cu alloy comprised of performing continuous casting by an intermittent pulling out method, by use of any one of the molds described in (1) to (5) above.
  • a continuous casting method of a Cu alloy according to (6) above comprised of giving, at the time of continuously casting the Cu alloy by an intermittent pulling out method, a vibration that has a frequency larger than the intermittent pulling out frequency by two orders or more and that has a component vertical to the pulling out direction of the slab.
  • a continuous casting method of a. Cu alloy according to (6) or (7) above comprised of continuously supplying, at the time of continuously casting the Cu alloy by an intermittent pulling out method, a lubricant or an anti-sticking material between the inner wall of the mold and the slab.
  • (10) A continuous casting method of a Cu alloy according to any one of (6) to (9) above, wherein the Cu alloy contains, by mass %, one or more components selected from Cr: 0.01 to 5%, Ti: 0.01 to 5%, Zr: 0.01 to 5%, Nb: 0.01 to 5%, Ta: 0.01 to 5%, Al: 0.01 to 5%, Mo: 0.01 to 5%, V: 0.01 to 5%, Co: 0.01 to 5%, Mn: 0.01 to 5%, Si: 0.01 to 5%, Be: 0.01 to 5%, and Hf: 0.01 to 5%.
  • First group 0.001 to 1 mass % in total of one or more selected from P, B, Sb, Bi, Pb, Cd, S and As;
  • Second group 0.01 to 5 mass % in total of one or more selected from Sn, Ag, Zn, Ni, Au, Pd, Fe, W, In and Ge; and
  • Third group 0.01 to 3 mass % in total of one or more selected from Te, Se, Sr, Tl, Rb, Cs, Ba, Re, Os, Rh, Po, Ga, Tc, Ru, Pd, Ir, Pt and Ta.
  • a continuous casting mold capable of continuously and stably producing a sound slab.
  • a continuous casting method of a Cu alloy capable of ensuring excellent characteristics such as strength, electric conductivity, bending workability and fatigue strength of the final product after working and heat treatment, can be provided.
  • a Cu alloy containing Zr, Ti, Cr, Ta, V and so on which are elements that easily form into carbides, a profound effect can be obtained.
  • the present invention is highly effective not only for Cu alloys but also for such materials as non-ferrous metals other than Cu alloys.
  • FIGS. 1 to 7 Examples of a mold for a direct-connection type of horizontal continuous casting according to the present invention, are shown in FIGS. 1 to 7 .
  • the mold is directly connected to a refractory constructing the holding furnace wall 2 that stores a Cu alloy melt 1 .
  • a connecting refractory such as a feeding nozzle, may be provided between the holding furnace wall and the mold.
  • a cooling jacket 5 adapted to carry cooling water or the like into the mold, is arranged closely to the outside of a mold member 3 and/or another part of mold member 3 ′, in which heat extraction is performed by primarily cooling the Cu alloy melt, and the solidification proceeds to form into a slab 4 .
  • the slab 4 leaving the mold is subjected to secondary cooling 6 by water spray, air spray, air-water mixed spray or the like.
  • the slab 4 is pulled out in an arrowed direction 7 .
  • the mold according to the present invention may include a coating 8 applied to the inner wall of the mold in the solidification starting position 10 of the Cu alloy melt. It may include a coating 9 applied to the inner wall in the position of the mold, which is located at an upper stream part than the solidification starting position.
  • the mold may be composed of a plurality of parts of mold members, for example, a part of mold member 3 and another part of mold member 3 ′.
  • the mold inner wall might be deteriorated by oxidation at the time of preheating before casting.
  • an oxidation resisting coating such as metal plating, is preferably applied at least to the inner wall of the mold in the solidification starting position of the inner wall surface of the mold.
  • the oxidation resisting coating material is not particularly limited, but one easily soluble to the melt at the time of casting without deteriorating the characteristics or the like of the final product, is preferably used.
  • Cu is preferably used as the coating material, with a thickness of about several micrometers.
  • the solidification starting position in the present invention is defined as follows. In the mold, molten Cu alloy is fed from the holding furnace, and forms into a solidification shell in a certain position in the mold. This solidification shell forming position is called the solidification starting position.
  • the solidification starting position is slightly varied depending on the casting conditions such as the temperature of the melt in the holding furnace, the cooling condition in both primary and secondary stages, and the pulling out velocity and so on. Thus, the solidification starting position has a certain fluctuation in the pulling out direction.
  • FIGS. 1 to 7 show examples of the mold for a direct-connection type of horizontal continuous casting according to the present invention, while the mold for a direct connection type of vertical continuous casting can be shown by rotating these figures clockwise by 90°.
  • a continuous casting mold for a Cu alloy according to the present invention will be further described in detail in terms of types (A) to (E). Further, a method for continuously casting a Cu alloy by use of these molds will also be described.
  • FIG. 1 is a schematic view of a continuous casting mold for a Cu alloy as one example of the continuous casting mold, according to the present invention, using a glassy carbon or a metal-based self-lubricating composite material for the mold member 3 including the solidification starting position 10 of the Cu alloy melt.
  • a sound slab can be produced continuously, efficiently, and stably.
  • a continuous casting method of a Cu alloy capable of ensuring excellent characteristics such as strength, electric conductivity and fatigue strength of a final product after working and heat treatment, can be provided.
  • a Cu alloy containing elements such as Zr, Ti, Cr, Ta and V, which easily form into carbides, a profound effect can be obtained.
  • the present inventors found that, when the direct-connection type of continuous casting is executed using a mold member which is made of a conventional graphite material with a bulk density of 1.7 to 1.9, the Cu alloy melt penetrates into a number of open pores which are on the graphite surface, whereby the initially formed solidification shell is stuck to the mold, resulting in mold damage with increase of the pulling out resistance or sometimes into an interruption of process. It was also found that, when the melt contains elements such as Zr, Ti and Cr which are reactive with C, the formation of the carbides in the boundary between the melt and the mold further causes sticking of the initially formed solidification shell to the mold, resulting in mold damage due to mold biting or into an interruption of the slab pulling out process.
  • a glassy carbon or a metal-based self-lubricating composite material is effective from the viewpoint of the reaction between the mold material and the melt.
  • the glassy carbon material has characteristics of being, rarely oxidized, compared with the graphite, and also being rarely reactive with Zr, Ti, and Cr, and therefore, it was found that the purpose can be sufficiently attained.
  • the metal-based self-lubricating composite material means a cermet obtained by dispersing and mixing a self-lubricant such as MoS 2 , WS 2 , BN or mica that rarely reacts with Ti, Cr or Zr into a metal matrix.
  • This composite material can also sufficiently attain the purpose.
  • the method for producing the composite material is not particularly limited. For example, mixing a metal powder with a self-lubricant particle, followed by pressing and sintering, can produce the composite material.
  • the content of the self-lubricant in the composite material is not particularly limited, but is, by volume %, preferably 10% or more, more preferably 30% or more, and further preferably 80% or more.
  • the content is, by volume %, preferably controlled to 85% or less.
  • the metal constituting the composite material with the self-lubricant is not particularly limited, and any metal or alloy can be used. Use of a metal and/or an alloy having a high melting point and high thermal conductivity is preferred since the mold material makes contact with a Cu alloy melt.
  • the specific examples of the metal of the alloy are a Cu alloy, a stainless steel, a Ni alloy, a Co alloy, and a W alloy.
  • An increased vibration frequency is more preferable, and it is preferably set to 5000 cpm (83 Hz) or more, and more preferably to 60000 cpm (1 kHz) or more, which is close to the ultrasonic area.
  • a fine particle of MoS 2 , WS 2 , BN, mica, or carbon is recommended to be supplied between the mold inner wall and the slab.
  • a superfine particle of CaCO 3 which is difficult to agglomerate, is strongly recommended as the anti-sticking material.
  • the continuous supply thereof is performed, for example, by injecting a solution of the fine particle of the lubricant or anti-sticking material suspended in mineral oil, synthetic ester or a mixture thereof through a number of through-holes of about 20 ⁇ m provided in the mold inner wall by the use of a pressure pump. A sufficient effect can be obtained in an injection quantity of about 0.1 cc/cm 2 ⁇ min, which is as little as sweat.
  • a continuous casting mold for a Cu alloy composed of any one member selected from a graphite, a ceramic and a metal member or of a combination of two or more parts of members thereof, in which at least the inner wall in the solidification starting position of the Cu alloy melt is coated with a self-lubricant or a metal-based self-lubricating composite material:
  • FIG. 2 is a schematic view of a continuous casting mold for a Cu alloy as an example of the continuous casting mold according to the present invention, in which the mold member 3 is composed of any one member selected from a graphite, a ceramic and a metal, and in which a coating 8 of a self-lubricant or a metal-based self-lubricating composite material is applied to the inner wall in the solidification starting position 10 of the Cu alloy melt.
  • a mold which is composed of any one member selected from the graphite, the ceramic and the metal member, with a coating of the self-lubricant or the metal-based self-lubricating composite material applied to the inner wall of the mold, is used, whereby a sound slab can be continuously, efficiently and stably produced.
  • a continuous casting method of a Cu alloy capable of ensuring excellent characteristics such as strength, electric conductivity and fatigue strength of the final product after working and heat treatment, can be provided.
  • a Cu alloy containing elements such as Zr, Ti, Cr, Ta and V, which easily form into carbides, a profound effect can be obtained.
  • a compact coating material composed of C, for example, a glassy carbon, a layered carbon and a diamond-like carbon, which are self-lubricant materials, are preferably selected in order to enhance the adhesion between the mold material and the coating film. Since the surface unevenness of the coating film almost reflects the surface unevenness of the graphite itself, it is desirable to select a graphite with a bulk density as high as possible. Although the bulk density is not particularly limited, it is preferably 1.7 or more, more preferably 1.8 or more, or further preferably more than 1.92.
  • an inorganic material composed of one or more selected from oxides, nitrides, carbides and borides is used.
  • a BN material and a sialon material are preferable because of the mechanical strength and thermal conductivity to be provided as the mold material.
  • the thinner mold thickness that is, the narrower distance between the slab and a cooling jacket is preferably adapted.
  • a compact coating material composed of a nitride compound, for example, a BN material that is a self-lubricant is preferably selected in order to enhance the adhesion between the mold material and the coating film.
  • the metal is not particularly limited, and any metal or alloy can be used. Use of a metal or an alloy having a high melting point and high thermal conductivity is preferred, for example, a Cu alloy, a stainless steel, a Ni alloy, a Co alloy, a W alloy, since the mold material will make contact with the Cu alloy melt.
  • a metal-based compact coating material such as a metal-based self-lubricant material is preferably selected in order to enhance the adhesion between the mold material and the coating film.
  • the metal-based self-lubricating composite material means a cermet obtained by dispersing and mixing a self-lubricant such as MoS 2 , WS 2 , BN and mica that rarely reacts with Zr, Ti or Cr in a metal matrix. It was found that the purpose can be sufficiently attained by applying this to the metal or alloy used for the mold material by electroless plating, electrolytic plating or spray coating. After the coating, the surface is polished preferably with an emery paper of about No. 1000.
  • the content of the self-lubricant in the composite material (cermet) to be plated or sprayed is not particularly limited. However, although the reaction resistance and the lubricating property are improved, an increased content of the self-lubricant causes deterioration of the peeling resistance of the film, then the content is preferably set to about 10 to 30 vol. %.
  • the metal in the composite material to be coated by plating is not particularly limited, and any metal or alloy can be used. Particularly, use of a metal or an alloy having a high melting point and high thermal conductivity is preferred, for example, a Cu alloy, stainless steel, a Ni alloy, a Co alloy and a W alloy.
  • the similar effect can be obtained over a longer time.
  • An increased vibration frequency is more preferable, and the frequency is preferably set to 5000 cpm (83 Hz) or more, and more preferably to 60000 cpm (1 kHz) or more, which is close to the ultrasonic area.
  • the lubricant to be supplied between the inner wall of the mold and the slab is the same as described above.
  • a continuous casting mold for a Cu alloy composed of a combination of two or more parts of members selected from a self-lubricant, a metal-based self-lubricating composite, a graphite, a ceramic and a metal member, in which the self-lubricant or the metal-based self-lubricating composite member is used at least for the inner wall in the solidification starting position of the Cu alloy melt:
  • FIG. 3 is a schematic view of a continuous casting mold for a Cu alloy as an example of the continuous casting mold according to the present invention.
  • This is an example of the mold that is composed of a combination of plurality of parts, that is, the mold composed of a part of mold member 3 including an inner wall in the solidification starting position 10 of the Cu alloy melt, and another part of mold member 3 ′.
  • the self-lubricant or the metal-based self-lubricating composite member is used for the part of mold member 3 including the inner wall in the solidification starting position 10 of the Cu alloy melt, and any one member selected from the graphite, the ceramic and the metal member is used for the other part of mold member 3 ′.
  • the mold composed of a plurality of parts, that is, the mold composed of a combination of a part of mold member including an inner wall in the solidification starting position, using a self-lubricant or a metal-based self-lubricating composite material, and another part of mold member using any one of the selected from a self-lubricant, a metal-based self-lubricating composite, a graphite, a ceramic and a metal material, leads to a sound slab which can be continuously, efficiently and stably produced.
  • a continuous casting method of a Cu alloy ensuring excellent characteristics such as strength, electric conductivity, bending workability and fatigue strength of a final product after working and heat treatment can be provided.
  • a Cu alloy containing elements such as Zr, Ti, Cr, Ta and V that easily form into carbides, a profound effect can be obtained.
  • any of a glassy carbon, a layered carbon, a BN (example 22), and a metal-based self-lubricating composite member obtained by dispersing and mixing a self-lubricant such as MoS 2 , WS 2 , BN, or mica that rarely reacts with Zr, Ti or Cr in a metal matrix can be selected.
  • a self-lubricant such as MoS 2 , WS 2 , BN, or mica that rarely reacts with Zr, Ti or Cr in a metal matrix
  • a continuous casting mold for a Cu alloy composed of a combination of two or more parts of members selected from a self-lubricant, a metal-based self-lubricating composite, a graphite, a ceramic and a metal member, in which at least the inner wall in the solidification starting position of the Cu alloy melt is coated with a self-lubricant or a metal-based self-lubricating composite material:
  • FIG. 4 is a schematic view of a continuous casting mold for a Cu alloy as one example of the continuous casting mold according to the present invention, which is composed of a plurality of parts of members, and which has a coating 8 of a self-lubricant or a metal-based self-lubricating composite material applied to the inner wall of the mold in the solidification starting position 10 of the Cu alloy melt.
  • the mold is composed of a part of mold member 3 and another part of mold member 3 ′, using two kinds of parts of members selected from a metal-based self-lubricating composite, a graphite, a ceramic and a metal member.
  • the mold which is composed of a part of any one member of mold selected from a graphite, a ceramic and a metal member, and another downstream part of a metal-based self-lubricating composite or a graphite member, has a coating of the self-lubricant or the metal-based self-lubricating composite material applied to the inner wall in the solidification starting position of a Cu alloy melt.
  • the mold leads to a sound slab that can be continuously, efficiently and stably produced.
  • a continuous casting method of the Cu alloy ensuring excellent characteristics such as strength, electric conductivity, bending workability and fatigue strength of the final product after working and heat treatment, can be provided.
  • a Cu alloy containing elements such as Zr, Ti, Cr, Ta and V that easily form into carbides, a profound effect can be obtained.
  • the graphite member, the ceramic member, the metal member, and the metal-based self-lubricating composite member to be used for the mold member are the same as described above.
  • any of the glassy carbon, the layered carbon, and the BN which are self-lubricants and the metal-based self-lubricating composite member obtained by dispersing and mixing self-lubricants such as MoS 2 , WS 2 , BN and mica, that rarely react with Zr, Ti or Cr in a metal matrix, can be selected.
  • FIG. 5 Another example of the continuous casting mold according to the present invention, is shown in FIG. 5 .
  • the mold member 3 including a mold portion in the solidification starting position 10 of the Cu alloy melt is composed of a metal-based self-lubricating composite, and a coating 9 of a ceramic material is applied to the inner wall in the position that contacts with the Cu alloy melt in order to suppress the reaction with the melt.
  • the coating method of the ceramic can be applied by spraying, CVD, etc.
  • FIG. 6 The other example of the continuous casting mold according to the present invention, is shown in FIG. 6 .
  • This continuous casting mold for a Cu alloy is composed of a metal member for the mold member 3 . in which a coating 8 of the metal-based self-lubricating composite material is applied to the inner wall in the solidification starting position 10 of the Cu alloy melt, and a coating 9 of the ceramic is applied to the inner wall in the position of the mold that contacts with the Cu alloy melt in order to suppress the reaction with the melt.
  • the coating method of the ceramic is the same as described above.
  • This continuous casting mold for a Cu alloy is composed of an upstream part of mold of a metal member and another downstream part of mold of a graphite member.
  • the part of mold of a metal member has a coating 8 of a metal-based self-lubricating composite material applied to the inner wall in the solidification starting position 10 of the Cu alloy melt, and has a coating 9 of a ceramic material applied to the inner wall in the position of the mold that contacts with the Cu alloy melt in order to suppress the reaction with the melt.
  • the coating method of the ceramic is the same as described above.
  • the part of mold when the part of mold is composed of the metal or metal-based self-lubricating composite member, it is further effective to apply the coating of the ceramic to the inner wall in the position of the mold that contacts with the Cu alloy melt in order to avoid the reaction of the member with Zr, Ti, Cr and so on in the melt.
  • the coating method of ceramics it is recommended as the coating method of ceramics to apply a coating of a cushioning material about 50 ⁇ m thick (e.g., Ni plating, frame-coating of WC-27 wt % NiCr, and so on), and then apply a ceramic coating about 200 ⁇ m thick thereon by frame coating.
  • a ceramic composed of a further stable oxide, at a casting temperature of the Cu alloy of 1250° C. is preferred.
  • ZrO 2 -8 wt % Y 2 O 3 , ZrO 2 -25 wt % MgO, ZrO 2 -5 wt % CaO and so on are recommended since no adhesion of the Cu alloy is caused.
  • the inner wall in the position of the upstream part of mold to be coated is preliminarily ground so as not to form a difference in level after ceramic coating.
  • Cu alloys including Cu—Ti—X alloys (X: Cr, Fe, Co, Ta, Nb, Mo, V, Mn, Be, Si, Ni, Sn, Ag, etc.), Cu—Zr—X alloys (X: Cr, Fe, Co, Ta, Nb, Mo, V, Mn, Be, Si, Ni, Sn, Ag, etc.), and Cu—Ti—Zr alloys.
  • Some compounds such as Ti—Cr and Zr—Cr and some metals such as Ti, Zr and Cr precipitates in a certain high-temperature region in the cooling process after solidification, which is apparent from the phase diagrams of Ti—Cr, Zr—Cr and Ti—Zr binary alloy systems shown in FIGS. 8, 9 and 10 .
  • These precipitates formed in a certain high-temperature region in the cooling process after solidification tend to be coarsened or aggregated, and it is quite difficult to dissolve them by the subsequent solution treatment, which is apparent from the phase diagrams.
  • a slab or bloom, according to the present invention has a profound effect through the process of working such as rolling at 600° C. or lower and an aging treatment in the temperature region of 150 to 750° C., without a hot process such as hot rolling and solution treatment described in the above-mentioned Patent Document 1.
  • the alloy is strengthened by a fine precipitation of an intermetallic compound between Cu and an alloy element such as Cu 4 Ti and Zr 9 Cu 2 or between the alloy elements, or a fine metal precipitate of Ti, Zr, Cr and so on. Then, it is enhanced in electric conductivity by the resulting reduction of the dissolved elements such as Ti, Zr, and Cr that are harmful to electric conductivity.
  • the average cooling rate from the temperature of the start of solidification to 600° C. is preferably 1° C./s or more, and further preferably 10° C./s or more.
  • a Cu alloys according to the present invention include the Cu alloy containing, by mass %, one or more components selected from Cr: 0.01 to 5%, Ti: 0.01 to 5%, Zr: 0.01 to 5%, Nb: 0.01 to 5%, Ta: 0.01 to 5%, Al: 0.01 to 5%, Mo: 0.01 to 5%, V: 0.01 to 5%, Co: 0.01 to 5%, Mn: 0.01 to 5%, Si: 0.01 to 5%, Be: 0.01 to 5%, and Hf: 0.01 to 5%.
  • a Cu alloy containing, in addition to the above components, by mass %, 0.001 to 5 mass % in total of one or more of the alloy components selected from at least one group of the following three groups is given:
  • First group 0.001 to 1 mass % in total of one or more selected from P, B, Sb, Bi, Pb, Cd, S and As;
  • Second group 0.01 to 5 mass % in total of one or more selected from Sn, Ag, Zn, Ni, Au, Pd, Fe, W, In and Ge; and
  • Third group 0.01 to 3 mass % in total of one or more selected from Te, Se, Sr, Ti, Rb, Cs, Ba, Re, Os, Rh, Po, Ga, Tc, Ru, Pd, Ir, Pt and Ta.
  • a Cu alloy further containing 0.001 to 2 mass % in total of one or more alloy components selected from Li, Ca, Mg and rare earth elements is also given.
  • the rare earth elements include Sc, Y and lanthanoide, and each element may be added alone as raw material or in a form of mish metal.
  • a Cu alloy with given chemical composition Prior to continuous casting using the mold according to the present invention, a Cu alloy with given chemical composition is prepared by a melting furnace.
  • the melting is desirably performed under a non-oxidizing atmosphere. While the melting is inevitably performed in the air, it is effective to suppress the oxidation by shrouding the melt by a flux (e.g., cryolite, fluorite, etc.) or charcoal particles.
  • the melt is poured into a holding furnace.
  • the melting is desirably conducted using the holding furnace in order to suppress the oxidation during the pouring.
  • Any of horizontal type, vertical type and so on can be adapted to this continuous casting if it is the direct-connection type of continuous casting using the mold directly connected to a holding furnace.
  • the mold according to the present invention has minimized operational problems in the production of the Cu alloy according to the present invention because of the low reactivity with the melt and a satisfactory lubricating property.
  • the inner wall in the vicinity of the solidification starting position in the mold is gradually thinned by the reaction with the melt or abrasion, the slab might be caught thereby and not easily pulled out. In such a case, it is effective to uniformly thin the inner wall by adjusting the cooling condition of the mold, the pulling out rate, or the like and moving the solidification position.
  • the slab is intermittently pulled out.
  • the higher cooling rate in the cooling process after solidification is desirable based on the above-mentioned reason. Particularly, it is desirable to take measure to raise the cooling rate in the secondary cooling zone corresponding to the temperature range of coarsened or agglomerated precipitation. Specifically, it is effective to employ water spray, air spray, or air-water mixed spray just after leaving the mold
  • the final product is obtained by a combination of working such as rolling at 600° C. or lower and the aging treatment at 150 to 750° C. This working may be performed, of course, in the cooling process after continuous casting.
  • Cu alloys containing 2.0 ⁇ 0.1 wt % of Ti, 1.0 ⁇ 0.1 wt % of Cr, 0.4 ⁇ 0.02 wt % of Sn, and 0.1 ⁇ 0.01 wt % of Zn were melted in a high frequency vacuum melting furnace, and a continuous casting test was carried out in 30 kinds of various production methods shown in Tables 1 and 2.
  • Each Cu alloy melt was transferred to a holding furnace, and a slab of 20 mm ⁇ 200 mm section was intermittently pulled out in a predetermined condition while holding the temperature of the furnace at 1250° C.
  • graphite was used as a refractory of the melting furnace and the holding furnace.
  • the oxidation of the melt was suppressed by an Ar gas flow during pouring in addition to charcoal covering.
  • a water-cooled jacket composed of the Cu alloy was located adjacent to the mold in order to perform primary cooling, and the slab leaving the mold was cooled again by an air-water mixed spray.
  • the temperature measurement was performed basically after leaving the mold by use of a thermocouple or radiation thermometer. In some cases, the mold temperature was measured by boring a through-hole from the mold outer wall to a position 5 mm inside and inserting the thermocouple. Using both the measured data and the physical properties of each mold material, whereby the solidification starting position was estimated, performed a heat transfer analysis. The average cooling rate from the solidification start point to 600° C. was calculated based on the above data. In the tests shown in Tables 1 and 2, the cooling rate was controlled to the range of 5 ⁇ 2° C.
  • Amplitude casting 5 ⁇ m 8 The Present Mold composed of a metal-based self-lubricating Non MoS 2 fine 258 60 m Satisfactory Invention, composite member obtained by dispersing WS 2 + BN particle + Mineral Complete (85 vol %) to W alloy followed by sintering. oil casting 9 The Present Mold composed of a metal-based self-lubricating Frequency MoS 2 fine 258 60 m Satisfactory Invention, composite member obtained by dispersing WS 2 + BN 5 kHz particle + Mineral Complete (85 vol %) to W alloy followed by sintering.
  • Amplitude oil casting 5 ⁇ m 10 The Present Mold composed of a graphite member with bulk Non Non 258 60 m Excellent Invention, density of 1.82 with coating of a glassy carbon Complete material applied to the inner wall.
  • casting 11 The Present Mold composed of a graphite member with bulk Non Non 258 60 m Satisfactory Invention, density of 1.82 with coating of a layered carbon Complete applied to the inner wall.
  • casting 12 The Present Mold composed of a ceramic member obtained by Non Non 258 60 m Satisfactory Invention, sintering sialone (30 vol %) and BN (70 vol %) with Complete coating of BN applied to the inner wall by CVD.
  • the Present Mold composed of a W alloy member with coating of Non Non 258 60 m Satisfactory Invention, a metal-based self-lubricating composite material Complete obtained by dispersing WS 2 + BN to W alloy, applied casting to the inner wall by plating.
  • the Present Mold composed of a ceramic member obtained by Frequency Non 258 60 m Satisfactory Invention, sintering sialone (30 vol %) and BN (70 vol %), with 5 kHz Complete coating of BN applied to the inner wall by CVD.
  • Amplitude oil casting 5 ⁇ m 17 The Present Mold composed of a W alloy member with coating of Frequency Non 258 60 m Satisfactory Invention, a metal-based self-lubricating composite material 5 kHz Complete obtained by dispersing WS 2 + BN to W alloy, applied Amplitude casting to the inner wall by plating. 5 ⁇ m 18
  • the Present Mold composed of a combination of a part of a BN Non Non 258 60 m Satisfactory Invention, member including the inner wall in the Complete solidification starting position and another part casting of a ceramic member obtained by sintering sialone (30 vol %) and BN (70 vol %).
  • the Present Mold composed of a combination of a part of a Non Non 258 60 m Satisfactory Invention metal-based self-lubricating composite member Complete obtained by dispersing WS 2 + BN (85 vol %) to W alloy, casting including the inner wall in the solidification starting position, and another part of a Cu—Cr alloy member.
  • the Present Mold composed of a combination of a part of a Non Non 258 60 m Satisfactory Invention, ceramic member obtained by sintering sialone Complete (30 vol %) and BN (70 vol %) with a CVD coating of casting BN, and another part of a graphite member with bulk density of 1.82.
  • the Present Mold composed of a combination of a part of a W Non Non 258 60 m Satisfactory Invention, alloy member obtained by dispersing WS 2 + BN to W Complete alloy with a plate coating of a metal-based casting self-lubricating composite material, and another part of a graphite member with bulk density of 1.82.
  • the Present Mold composed of a combination of an upstream part Non Non 258 60 m Satisfactory Invention, of a W alloy member with a plate coating of a Complete metal-based self-lubricating composite material casting obtained by dispersing WS 2 + BN to W alloy applied to the inner wall in the solidification starting position, and with a sprayed ZrO 2 —8 wt % Y 2 O3 applied to the inner wall in the upper stream position including the solidification starting position, and a downstream part of a graphite member with bulk density of 1.83.
  • 34 Comparative Mold composed of a natural graphite member.
  • Non Non 258 3 m Frequent Interrupt of occurrence of pulling out pulling out due to slab mark crack failure 35 Comparative Mold composed of a graphite member with bulk Non Non 258 3 m Frequent density of 1.77. Interrupt of occurrence of pulling out pulling out due to slab mark crack failure 36 Comparative Mold composed of graphite member with bulk Non Non 258 4 m Frequent density of 1.82. Interrupt of occurrence of pulling out pulling out due to slab mark crack failure 37 Comparative Mold composed of a graphite member with bulk Non Non 258 8 m Frequent density of 1.90. Interrupt of occurrence of pulling out pulling out due to slab mark crack failure
  • the casting was intended to ensure a length of about 60 m upon completion. However, due to an abnormal rise of pulling out resistance because of mold biting in the initial solidification shell was observed in some cases in the middle of the pulling out. The quality of the slab surface was evaluated by visually determining flaws thereon.
  • casting 40 The present 3 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 41 The present 4 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 42 The present 5 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 43 The present 6 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 44 The present 7 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 45 The present 8 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 46 The present 9 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 47 The present 10 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 48 The present 11 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 49 The present 12 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 50 The present 13 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 51 The present 14 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 52 The present 15 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 53 The present 16 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 54 The present 17 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 55 The present 18 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 56 The present 19 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 57 The present 20 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 58 The present 21 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 61 The present 24 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 62 The present 25 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 63 The present 26 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 64 The present 27 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 65 The present 28 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 66 The present 29 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 67 The present 30 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 68 The present 31 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 69 The present 32 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 70 The present 33 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 71 The present 34 Mold composed of a graphite member with bulk density of Non Non 258 60 m Excellent invention, 1.83, with a coating of a glassy carbon material applied to Complete the inner wall in the solidification starting position.
  • casting 73 The present 3 Mold composed of a combination of a part of a glassy Non Non 258 60 m Excellent invention, carbon member including the solidification starting Complete position, and another part of a graphite member with bulk casting density of 1.83.
  • test piece 13 B according to the regulation of JIS Z 2201, was collected from each specimen, and the tensile strength [TS (MPa)] at room temperature (25° C.) was determined according to the method regulated in JIS Z 2241.
  • a test piece with width of 10 mm ⁇ length of 60 mm was prepared from each specimen, current was carried in the longitudinal direction of the test piece in order to measure the potential difference between both ends of the test piece, and the electric resistance was determined by a 4-terminal method. Successively, the electric resistance (resistivity) per unit volume was calculated from the volume of the test piece that was measured by a micrometer, and the electric conductivity [IACS (%)] was determined from its ratio to resistivity 1.72 ⁇ cm of a reference sample obtained by annealing polycrystalline pure copper.
  • the “high tensile strength in relation with conductivity” means a state satisfying the following equation (1) (this state is hereinafter referred to as “well-balanced state of tensile strength and electric conductivity”): TS ⁇ k 10 +k 11 ⁇ exp( ⁇ k 12 ⁇ IACS ) (1)
  • TS tensile strength (MPa)
  • IACS electric conductivity (%)
  • IACS means the percentage to the electric conductivity of the pure copper polycrystalline material.
  • the present invention involves a continuous casting mold used mainly for a direct-connection type of continuous casting, with a mold directly connected to a holding furnace, and a continuous casting method of a Cu alloy.
  • the present invention provides a mold capable of continuously and efficiently producing a sound slab or bloom, and also a continuous casting method of a Cu alloy which ensures excellent characteristics, such as strength, electric conductivity, vending workability, impact resistance and fatigue strength of the final product after working and heat treatment.
  • the application of the production of the Cu alloy containing elements such as Zr, Ti, Cr, Ta and V that easily generate carbides provides a profound effect.
  • FIG. 1 An example of a continuous casting mold according to the present invention.
  • FIG. 2 An example of the continuous casting mold according to the present invention, which has a coating 8 of a self-lubricant or a metal-based self-lubricating composite material applied to the mold inner wall in the solidification starting position of a Cu alloy melt.
  • FIG. 3 An example of the continuous casting mold according to the present invention, which is composed of a plurality of parts of mold members.
  • FIG. 4 An example of the continuous casting mold according to the present invention, which is composed of a plurality of parts of mold members, and has a coating 8 of a self-lubricant or metal-based self-lubricating composite material applied to the mold inner wall in the solidification starting position of an alloy melt.
  • FIG. 5 Another example of the continuous casting mold according to the present invention, which includes a coating 9 of ceramic material applied to the inner wall in the position that contacts with a Cu alloy melt in order to inhibit the reaction with the melt.
  • FIG. 6 Another example of the continuous casting mold according to the present invention, which has a coating 8 of a metal-based self-lubricating composite material applied to the mold inner wall in the solidification starting position of an alloy melt, and a coating 9 of a ceramic material applied to the inner wall in the position that contacts with a Cu alloy melt in order to inhibit reaction with the melt.
  • FIG. 7 Another example of the continuous casting mold according to the present invention, which is composed of an upstream part of a metal member and a downstream part of a graphite member, with a coating 8 of a metal-based self-lubricating composite material applied to the inner wall in the solidification starting position of an alloy melt, and with a coating 9 of a ceramic material applied to the inner wall in the position that contacts with a Cu alloy melt in order to inhibit the reaction with the melt.
  • FIG. 8 A phase diagram of a Ti—Cr alloy.
  • FIG. 9 A phase diagram of a Zr—Cr alloy.
  • FIG. 10 A phase diagram of a Ti—Zr alloy.

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US20090224443A1 (en) * 2008-03-05 2009-09-10 Rundquist Victor F Niobium as a protective barrier in molten metals
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WO2017170699A1 (fr) 2016-03-30 2017-10-05 三菱マテリアル株式会社 Alliage de cuivre pour équipement électronique et électrique, bande plate en alliage de cuivre pour équipement électronique et électrique, composant pour équipement électronique et électrique, terminal, barre omnibus et pièce mobile pour relais
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Citations (4)

* 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
US4183394A (en) * 1976-12-17 1980-01-15 Kreidler Werke Gmbh Method and apparatus for horizontal continuous casting
US5171491A (en) * 1986-02-04 1992-12-15 The Carborundum Company Method of producing near net shape fused cast refractories

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2634633C2 (de) * 1976-07-31 1984-07-05 Kabel- und Metallwerke Gutehoffnungshütte AG, 3000 Hannover Stranggießkokille aus einem Kupferwerkstoff, insbesondere zum Stranggießen von Stahl
JPS5785652A (en) * 1980-11-19 1982-05-28 Kawasaki Steel Corp Continuous casting method for hollow blank material for pipe making
JPS6058783B2 (ja) * 1982-01-20 1985-12-21 日本鉱業株式会社 半導体機器のリ−ド材用銅合金の製造方法
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
JPS61169149A (ja) * 1985-01-22 1986-07-30 Nippon Mining Co Ltd 連続鋳造方法
JPH026037A (ja) * 1988-06-27 1990-01-10 Nkk Corp 鋼の連続鋳造方法
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
JP3013461B2 (ja) * 1991-02-22 2000-02-28 日立電線株式会社 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
JP3504129B2 (ja) * 1997-11-13 2004-03-08 東海カーボン株式会社 銅合金系連続鋳造用黒鉛鋳型
CH695210A5 (de) * 2000-12-11 2006-01-31 Concast Ag Kokille zum Stranggiessen einer Stahlschmelze.

Patent Citations (4)

* 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
US4183394A (en) * 1976-12-17 1980-01-15 Kreidler Werke Gmbh Method and apparatus for horizontal continuous casting
US5171491A (en) * 1986-02-04 1992-12-15 The Carborundum Company Method of producing near net shape fused cast refractories

Cited By (31)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8844897B2 (en) * 2008-03-05 2014-09-30 Southwire Company, Llc Niobium as a protective barrier in molten metals
US20090224443A1 (en) * 2008-03-05 2009-09-10 Rundquist Victor F Niobium as a protective barrier in molten metals
US9327347B2 (en) 2008-03-05 2016-05-03 Southwire Company, Llc Niobium as a protective barrier in molten metals
US8574336B2 (en) 2010-04-09 2013-11-05 Southwire Company Ultrasonic degassing of molten metals
US8652397B2 (en) 2010-04-09 2014-02-18 Southwire Company Ultrasonic device with integrated gas delivery system
US9617617B2 (en) 2010-04-09 2017-04-11 Southwire Company, Llc Ultrasonic degassing of molten metals
US10640846B2 (en) 2010-04-09 2020-05-05 Southwire Company, Llc Ultrasonic degassing of molten metals
US9382598B2 (en) 2010-04-09 2016-07-05 Southwire Company, Llc Ultrasonic device with integrated gas delivery system
US9121084B2 (en) * 2012-02-24 2015-09-01 Kobe Steel, Ltd. Copper alloy
US20130224070A1 (en) * 2012-02-24 2013-08-29 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Copper alloy
CN103114222A (zh) * 2013-03-14 2013-05-22 上海天申铜业集团有限公司 一种无铅水表及其表壳的铸造方法
US10316387B2 (en) 2013-11-18 2019-06-11 Southwire Company, Llc Ultrasonic probes with gas outlets for degassing of molten metals
US9528167B2 (en) 2013-11-18 2016-12-27 Southwire Company, Llc Ultrasonic probes with gas outlets for degassing of molten metals
US20170292181A1 (en) * 2014-09-25 2017-10-12 Mitsubishi Materials Corporation CASTING MOLD MATERIAL AND Cu-Cr-Zr ALLOY MATERIAL
US10544495B2 (en) * 2014-09-25 2020-01-28 Mitsubishi Materials Corporation Casting mold material and Cu—Cr—Zr alloy material
CN104475468A (zh) * 2014-12-09 2015-04-01 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
US10092970B2 (en) * 2015-01-09 2018-10-09 Jx Nippon Mining & Metals Corporation Titanium-copper alloy having plating layer
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
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KR101830841B1 (ko) 2016-11-29 2018-02-22 한국생산기술연구원 고내마모성을 갖는 싱크로나이저 링용 동합금 및 이의 제조방법
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US11440086B2 (en) 2020-03-30 2022-09-13 Ngk Insulators, Ltd. Method for producing Cu—Ni—Sn alloy and cooler to be used for same
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