EP3282027A1 - Matériau de fil d'acier à haute teneur en carbone présentant une excellente aptitude à l'étirage de fil et fil d'acier - Google Patents

Matériau de fil d'acier à haute teneur en carbone présentant une excellente aptitude à l'étirage de fil et fil d'acier Download PDF

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EP3282027A1
EP3282027A1 EP16772782.5A EP16772782A EP3282027A1 EP 3282027 A1 EP3282027 A1 EP 3282027A1 EP 16772782 A EP16772782 A EP 16772782A EP 3282027 A1 EP3282027 A1 EP 3282027A1
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Prior art keywords
wire
less
steel wire
pearlite
proeutectoid cementite
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EP3282027A4 (fr
EP3282027B1 (fr
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Tomonobu Ishida
Tomokazu Masuda
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Kobe Steel Ltd
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Kobe Steel Ltd
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
    • B21C1/02—Drawing metal wire or like flexible metallic material by drawing machines or apparatus in which the drawing action is effected by drums
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/001—Heat treatment of ferrous alloys containing Ni
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
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    • C21—METALLURGY OF IRON
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/64—Patenting furnaces
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
    • B21C1/003—Drawing materials of special alloys so far as the composition of the alloy requires or permits special drawing methods or sequences
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/003—Cementite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to a high-carbon steel wire rod with excellent wire drawability, and a steel wire obtained by wire drawing of the high-carbon steel wire rod mentioned above. More particularly, the present invention relates to a high-carbon steel wire rod produced by hot rolling, which is a raw material of a high strength steel wire to be used mainly for steel cords, wire ropes, saw wires and the like.
  • a high strength steel wire used for steel cords, wire rope and the like for example, piano wires mentioned in JIS G 3522(1991).
  • the piano wires are roughly classified into three types such as classes A, B, and V, and examples of the high strength piano wire class B include SWP-class B having a wire diameter of 0.2 mm and a tensile strength of 2,840 to 3,090 MPa.
  • SWP-class B having a wire diameter of 0.2 mm and a tensile strength of 2,840 to 3,090 MPa.
  • pearlite steels such as SWRS82A mentioned in JIS G 3502 (2004) are used as the raw material of the piano wire.
  • a common method for producing a high strength steel wire is as follows. First, a steel wire rod produced by hot rolling (also referred to as the rolled wire rod) is placed in a ring shape on a cooling conveyor, thereby allowing to undergo pearlite transformation, and then coiled into a coil shape to obtain a wire rod coil. Then, wire drawing is performed and a steel wire having desired wire diameter and strength is obtained by making use of the work hardening function of pearlite. When it is impossible to be drawn to a desired wire diameter due to working limit of the steel wire rod, a heat treatment called patenting is applied between wire drawings. For example, to obtain an extra fine steel wire having a wire diameter of 0.2 mm, wire drawing and a patenting treatment are generally performed by repeating several times.
  • Patent Document 1 relates to a wire rod for a high strength steel wire which is useful as the raw material of a galvanized steel wire to be used for ropes for a bridge, and particularly mentions a wire rod for a high strength steel wire, which is excellent in workability when wire drawing is performed by so-called cold drawing without subjecting to a heat treatment after rolling.
  • precipitation of proeutectoid cementite is suppressed by precipitating fine TiC near grain boundaries, so that the lower limit of the Ti content is set at 0.02% or more.
  • Patent Document 2 relates to a small diameter high-carbon hot-rolled wire rod which is capable of wire drawing at true strain of 2.2 or more even in an as-hot-rolled state. Specifically, Patent Document 2 mentions that a steel billet having the Si content suppressed to 0.50% or less is thinned to a wire rod diameter of 4.5 mm or less by increasing rolling reduction during hot rolling, thereby making austenite grains ( ⁇ grains) finer leading to acceleration of pearlite transformation, thus making it possible to prevent precipitation of particles of proeutectoid ferrite and proeutectoid cementite.
  • Patent Document 3 relates to a deformed wire for a submarine optical fiber cable in which a wire rod for a high tensile steel wire is used. Specifically, Patent Document 3 mentions that, by using a wire rod in which Si is segregated so as to satisfy the following inequality expression: Si maximum segregation degree of cementite/ferrite interface in a range of 30 nm from an interface between cementite and ferrite to a ferrite phase side in a pearlite structure (maximum Si concentration in a range of 30 nm from an interface between cementite and ferrite to a ferrite phase side / Si content of bulk) ⁇ 1.1, it is possible to prevent wire breakage during deformation working.
  • Patent Documents 1 to 3 respectively have the following problems.
  • Patent Document 1 is intended for a wire rod to be used for a galvanized steel wire, and is not intended for a steel wire having an extra fine wire diameter of approximately 0.2 mm, such as a piano wire.
  • Patent Document 1 when an extra fine steel wire is produced using a wire rod having a large Ti content, wire breakage during wire drawing becomes remarkable due to Ti based inclusions. Therefore, it is difficult to apply the technique of Patent Document 1 to the extra fine steel wire to be supplied for steel cords.
  • Patent Document 2 when using a wire rod having a diameter of 4.5 mm or less, the productivity is degraded to cause a problem that wire rods are easily entangled with each other during the production of a coil.
  • Patent Document 3 when using a method in which an Si concentration difference is applied at an interface between cementite and ferrite in the pearlite structure, it is impossible to sufficiently reduce proeutectoid ferrite which is harmful for the wire drawability.
  • the degree of working carried out in Patent Document 3 is 82.6% in terms of an area reduction rate even when summing up wire drawing and cold rolling. Since the area reduction rate of wire drawing required to an extra fine steel wire such as a steel cord is larger, it is insufficient to apply the extra fine steel wire to the above-mentioned applications.
  • the present invention has been made in light of the foregoing circumstance, and it is an object of the present invention to provide a high-carbon steel wire rod with excellent wire drawability which can also be applied to extra fine steel wires such as steel cord, and a steel wire.
  • the present invention that can solve the foregoing problems provides a high-carbon steel wire rod including, in % by mass, C: 0.90 to 1.3%, Si: 0.4 to 1.2%, Mn: 0.2 to 1.5%, P: more than 0% and 0.02% or less, S: more than 0% and 0.02% or less, Al: more than 0% and 0.008% or less, Ti: 0 to 0.005%, and N: 0.001 to 0.008%, with the balance being iron and inevitable impurities, wherein the structure includes pearlite and proeutectoid cementite, an area ratio of pearlite is 90% or more relative to the entire structure, a maximum length of proeutectoid cementite is 15 ⁇ m or less, and a concentration difference between an average of the Si concentration inside proeutectoid cementite and a maximum value of the Si concentration inside ferrite that forms a lamellar structure of pearlite is 0.50 to 3%.
  • the above-mentioned high-carbon steel wire includes: in % by mass, at least one belonging to any one of the following (a) to (d):
  • a steel wire obtained by wire drawing of the above-mentioned high-carbon steel wire rod is also included in the scope of the present invention.
  • the present invention can provide a high-carbon steel wire rod with excellent wire drawability which can also be applied to extra fine steel wires such as steel cord.
  • Fig. 1 is a diagram showing an Si concentration difference at an interface between a proeutectoid cementite phase and a ferrite phase in the sample of test No. 12 in Table 2 of Example.
  • the inventors of the present invention have intensively studied using a high-carbon steel wire rod having the C content of 0.90% or more.
  • ferrite an Si concentration difference of 0.50% or more at an interface between proeutectoid cementite and ferrite that forms a lamellar structure of pearlite (hereinafter may be simply referred to as ferrite)
  • ferrite an Si concentration difference between an average of the Si concentration inside proeutectoid cementite, and a maximum value of the Si concentration inside ferrite is 0.50% or more
  • Patent Document 3 There is also some mention of Si segregation in Patent Document 3.
  • the Si concentration difference at an interface between cementite (lamellar cementite that forms a lamellar structure of pearlite) and ferrite in a pearlite structure is controlled, and the cementite is not. Therefore, on this point, the invention of Patent Document 3, and the present invention in which the Si concentration at an interface between proeutectoid cementite that is not cementite in the pearlite structure and ferrite is controlled, differ in structure of interest.
  • the cementite in the pearlite structure is essentially different from proeutectoid cementite, and the precipitation starting temperature of proeutectoid cementite is approximately 750°C and is higher than that of pearlite that precipitates at approximately 590 to 650°C. Therefore, it is considered that proeutectoid cementite which is harmful for the wire drawability cannot be sufficiently reduced by the technique of Patent Document 3.
  • Patent Document 3 also mentions that it is effective to set a rate of blast cooling after rolling of the wire rod at 1 to 10°C/second so as to efficiently segregate Si to the above-mentioned interface, and blast cooling at approximately 7°C/second is performed in all Examples.
  • components in the steel of the steel wire rod according to the present invention are as follows. Unit of each component is % by mass unless otherwise specified.
  • Carbon (C) is effective in increasing the strength, and the strength of the steel wire after cold working increases with the increase of the C content.
  • the lower limit of the C content is set at 0.90% or more, preferably 0.93% or more, and more preferably 0.95% or more. Any excessive C content, however, cannot achieve sufficient reduction of proeutectoid cementite which is harmful for the wire drawability, thus degrading the wire drawability. Therefore, the upper limit of the C content is set at 1.3% or less, and preferably 1.25% or less.
  • Silicon (Si) is an effective deoxidizing agent and has not only the effect of reducing oxide based inclusions in the steel, but also the effect of increasing the strength of the steel wire rod. As mentioned later, Si also has the effect of suppressing the growth of proeutectoid cementite. To effectively exhibit these effects, the lower limit of the Si content is set at 0.4% or more, preferably 0.45% or more, more preferably more than 0.50%, and still more preferably 0.55% or more. Addition of excessive Si accelerates the embrittlement during wire drawing, thus degrading twisting properties of the drawn wire rod. Therefore, the upper limit of the Si content is set at 1.2% or less, and preferably 1.15% or less.
  • Manganese (Mn) has the effect of extremely improving the hardenability of the steel, thus lowering the transformation temperature during blast cooling, leading to increased strength of the pearlite structure.
  • the lower limit of the Mn content is set at 0.2% or more, and preferably 0.3% or more.
  • Mn is an element which easily segregates into the center of the wire rod and addition of excessive Mn excessively enhances the hardenability of a Mn segregation portion, which may form a supercooled structure such as martensite. Therefore, the upper limit of the Mn content is set at 1.5% or less, preferably 1.0% or less, and more preferably 0.95% or less.
  • Phosphorus (P) is contained as impurities, and segregates in the prior austenite grain boundary to thereby cause embrittlement, leading to steel billet cracking and degradation of fatigue-resistant characteristics of the steel wire after wire drawing. Therefore, to prevent these harmful influences, the upper limit of the P content is set at 0. 02% or less, and preferably 0.018% or less. It is difficult to set the lower limit of the P content at 0% in view of industrial production.
  • the upper limit of the S content is set at 0.02% or less, and preferably 0.018% or less. It is difficult to set the lower limit of the S content at 0% in view of industrial production.
  • Al more than 0% and 0.008% or less
  • Aluminum (Al) is contained as impurities, and forms Al based inclusions such as Al 2 O 3 to thereby increase a wire breakage ratio during wire drawing. Therefore, to ensure sufficient wire drawability, the upper limit of the Al content is set at 0.008% or less, and preferably 0.006% or less. It is difficult to set the lower limit of the Al content at 0% in view of industrial production.
  • Titanium (Ti) is contained as impurities, and forms Ti based inclusions such as TiN to thereby increase a wire breakage ratio during wire drawing. Therefore, to ensure sufficient wire drawability, the upper limit of the Ti content is set at 0.005% or less, and preferably 0.003% or less.
  • the upper limit of the N content is set at 0.008% or less, and preferably 0.007% or less.
  • the steel wire rod of the present invention contains components mentioned above, the balance being iron and inevitable impurities.
  • the steel wire rod of the present invention can further include the following selective elements.
  • Boron (B) has the effect of concentrating on the austenite grain boundary to thereby prevent the formation of grain boundary ferrite, thus improving the wire drawability.
  • B also has the effect of chemically combining with N to form nitrides such as BN, and suppressing the degradation of the toughness due to solid-soluted N, thus improving twisting properties.
  • the lower limit of the B content is preferably set at 0.0005% or more. Addition of excessive B causes cracking during hot rolling as a result of the precipitation of a compound with Fe (B-constituent), so that the upper limit of the B content is preferably set at 0.01% or less, and more preferably 0.008% or less.
  • Co Cobalt
  • the wire drawability is accelerated by adding Co, in addition to Si.
  • the lower limit of the Co content is preferably set at 0.05% or more, and more preferably 0.1%.
  • the upper limit of the Co content is preferably set at 1.5% or less, more preferably 1.3% or less, and still more preferably 1% or less.
  • Vanadium (V) and chromium (Cr) are elements contributing to improve the strength of the steel wire rod. These elements may be added alone or used in combination.
  • V has the effect of increasing the strength due to the formation of fine carbonitrides, and also can exhibit the effect of improving twisting properties due to the reduction of solid-soluted N.
  • the lower limit of the V content is preferably set at 0.05% or more, and more preferably 0.1% or more.
  • V is an expensive element and the effect is saturated even if being added excessively, resulting in economic waste. Therefore, the upper limit of the V content is preferably set at 0.5% or less, and more preferably 0.4% or less.
  • the Cr has the effect of making lamellar spacing of pearlite finer to thereby enhance the strength of the steel wire rod.
  • the lower limit of the Cr content is preferably set at 0.05% or more, and more preferably 0.1% or more.
  • the upper limit of the Cr content is preferably set at 0.5% or less, and more preferably 0.4% or less.
  • Cu copper
  • MD mechanical descaling
  • Nickel (Ni) has the effect of enhancing the corrosion resistance of the steel wire rod.
  • the lower limit of the Ni content is preferably set at 0.05% or more. The effect is saturated even if being added excessively, resulting in economic waste. Therefore, the upper limit of the Ni content is preferably set at 0.5% or less, and more preferably 0.4% or less.
  • Niobium (Nb) has the effect of making crystal grains finer to thereby enhance the ductility of the wire rod.
  • the lower limit of the Nb content is preferably set at 0.05% or more.
  • the upper limit of the Nb content is preferably set at 0.5% or less, and more preferably 0.4% or less.
  • the steel wire rod of the present invention includes pearlite and proeutectoid cementite, and an area ratio of pearlite is 90% or more relative to the entire structure, a maximum length of proeutectoid cementite is 15 ⁇ m or less, and a concentration difference between an average of the Si concentration inside proeutectoid cementite and a maximum value of the Si concentration inside ferrite (hereinafter may simply referred to as the Si concentration difference) is 0.50 to 3%.
  • the steel wire rod of the present invention includes pearlite and proeutectoid cementite. Since the low temperature transformation structure, such as bainite or martensite (may also be referred to as the supercooled structure) inhibits the wire drawability, an area ratio of the pearlite structure is set at 90% or more, and preferably 95% or more, so as to ensure sufficient wire drawability.
  • the upper limit may be appropriately controlled depending on a relation with proeutectoid cementite, and is preferably approximately 99 area % or less.
  • the steel wire rod of the present invention can include, in addition to pearlite and proeutectoid cementite, the residual structure that is inevitably included during production process.
  • the residual structure include non-pearlite structures, such as bainite and proeutectoid ferrite.
  • the total content of the non-pearlite structure is preferably controlled to approximately 10 area % or less relative to the entire structure.
  • Proeutectoid cementite precipitating in a plate shape is the structure which is harmful for the wire drawability, and disturbs orientation of pearlite colonies of the steel wire rod and increases wire breakage as a starting point of cracking.
  • proeutectoid cementite having a short maximum length exert less harmful influences mentioned above.
  • Mechanism due to such proeutectoid cementite is as mentioned in detail in Patent Document 1.
  • the upper limit of the maximum length of proeutectoid cementite is set at 15 ⁇ m or less, preferably 13 ⁇ m or less, and more preferably 10 ⁇ m or less.
  • the lower limit of the maximum length of proeutectoid cementite is not particularly limited and may be, for example, approximately 0.1 ⁇ m.
  • Silicon (Si) is an element which is hardly solid-soluted in cementite and is discharged to an austenite phase from a cementite phase when proeutectoid cementite precipitates, and Si concentration difference is generated at the interface (interface between proeutectoid cementite and a ferrite phase).
  • the test results of the inventors revealed that, the more this Si concentration difference is large, the more the growth of a proeutectoid cementite phase is suppressed, thus enabling the reduction of the maximum length of proeutectoid cementite.
  • Si concentration distribution formed at this time is inherited even through subsequent pearlite transformation, so that observation of the structure of the thus produced steel wire rod leads to confirmation as an Si concentration difference at an interface between the proeutectoid cementite phase and the ferrite phase around the proeutectoid cementite phase.
  • a graph showing an Si concentration difference in the sample of test No. 12 in Table 2 of Example mentioned later is shown in Fig. 1 .
  • Fig. 1 an average of the Si concentration of the proeutectoid cementite phase in the center, and a maximum value of the Si concentration of each ferrite phase existing around the proeutectoid cementite phase are measured, and a difference therebetween is defined as the Si concentration difference.
  • the method for measuring the Si concentration will be mentioned in detail in the columns of Examples mentioned later.
  • the Si concentration difference calculated as mentioned above is set at 0.50% or more.
  • the maximum length of proeutectoid cementite can be set at 15 ⁇ m or less.
  • the Si concentration difference is preferably 0.6% or more. The effect mentioned above is saturated even if the Si concentration difference is excessively formed, so that the upper limit is set at 3% or less, and preferably 2.8% or less.
  • the Si concentration difference is generated at an interface between the proeutectoid cementite phase and ferrite in the pearlite structure, and the Si concentration difference is not generated at an interface between the proeutectoid cementite phase and the cementite (lamellar cementite that forms a lamellar structure of pearlite) phase in the pearlite structure.
  • the high-carbon steel wire rod as mentioned in the present invention is generally produced by the following procedure in which a steel billet with a predetermined chemical component adjusted in advance is austenitized by heating and then hot-rolled into a steel wire rod having a predetermined wire diameter.
  • the placing temperature is preferably set at 880 to 980°C.
  • the placing temperature is preferably 900°C or higher and 960°C or lower.
  • cooling is started at a temperature of 800°C or higher.
  • the cooling conditions are extremely important so as to control the desired Si concentration difference within a predetermined range. There is a need that the entire coil placed in a ring shape falls within the above-mentioned range of the cooling stop temperature and holding temperature.
  • cooling is performed to the cooling stop temperature of 480 to 620°C at an average cooling rate of 12 to 60°C/s.
  • the average cooling rate is low, the Si concentration difference generated at a proeutectoid cementite interface is lost by diffusion of Si atoms, thus failing to obtain the desired Si concentration difference.
  • the average cooling rate is high, a supercooled structure is formed and a pearlite area ratio becomes less than 90%.
  • the average cooling rate is more preferably 15°C/s or more and 55°C/s or less.
  • the cooling stop temperature is more preferably 500°C or higher and 600°C or lower.
  • the temperature is raised to the holding temperature of 590 to 650°C and pearlite transformation is performed.
  • the holding temperature is too high, Si atoms diffuse to thereby decrease the Si concentration difference. Meanwhile, when the holding temperature is too low, a supercooled structure is generated to thereby decrease the pearlite area ratio.
  • the holding temperature is more preferably 600°C or higher and 640°C or lower.
  • the steel wire rod of the present invention was obtained by the procedure mentioned above, and then coiled into a coil shape to obtain a wire rod coil. Then, wire drawing is performed to obtain a steel wire having desired wire diameter and strength.
  • a patenting treatment is preferably performed after wire drawing.
  • An extra fine steel wire having a wire diameter of approximately 0.2 mm can be obtained by further subjecting to wire drawing after the patenting treatment.
  • conditions of the patenting treatment There is no particular limitation on conditions of the patenting treatment and, for example, it is possible to employ conditions such as heating temperature of 950°C and patenting temperature of 600°C.
  • the patenting treatment may be performed not only once, but also plural times (for example, 2 to 3 times).
  • the thus obtained steel wire of the present invention has a high tensile strength such as approximately 4,000 MPa or more.
  • a steel wire having a wire diameter of approximately 0.1 to 0.4 mm is obtained, so that the thus obtained steel wire is suitably used for steel cords, wire ropes, saw wires and the like.
  • Each of steels A to Z (cross-sectional shape: 155 mm ⁇ 155 mm) shown in Table 1 was heated to a temperature of 1,000°C and hot-rolled into a predetermined wire diameter of 5.5 mm. Then, the hot-rolled steel was placed in a ring shape on a cooling conveyor and allowed to undergo pearlite transformation while control cooling by blast cooling, and then coiled into a coil shape to obtain a coil of rolled material.
  • the cooling conditions after rolling and the wire rod diameter after rolling are shown in Table 2.
  • the point counting method is a method in which the micrograph is sectioned into meshes and the number of structures existing in lattice points is counted to thereby easily determine an area ratio of the structure.
  • a micrograph of the center of the transverse section was taken at a magnification of 4,000 times to fabricate three SEM micrographs.
  • the each micrograph was sectioned into 100 lattice points and a pearlite area ratio was determined, and then an average was calculated.
  • An evaluation area of one SEM micrograph is 868 ⁇ m 2 .
  • the pearlite area ratio and details of the structure in each specimen are shown in Table 2.
  • the non-pearlite structure detected by the above point counting method (proeutectoid cementite structure, bainite structure) are also shown in Table 2.
  • P denotes a pearlite structure
  • B denotes a bainite structure
  • ⁇ denotes proeutectoid cementite.
  • one ring was collected from the coil end of the non-defective product and then divided into eight samples in a longitudinal direction.
  • a tensile test was performed and a tensile strength TS was measured. An average of the tensile strength of eight samples in total was determined, and then TS of the coil of rolled material was calculated.
  • the samples of tests Nos. 1 to 3, 11 to 21, and 24 to 32 are examples that satisfy the requirements of the present invention, and satisfactory wire drawability was confirmed without causing wire breakage.
  • all samples of tests Nos. 3, 11 to 14, 16 to 18, 20, and 21 in which steels C to G, I to K, M, and N, each containing B, in Table 1 are used wire drawing could be performed to high wire drawing strain without causing wire breakage.
  • samples of tests Nos. 11 and 12 in which steels D and E, each containing Co in addition to B, in Table 1 are used wire drawing could be performed to higher wire drawing strain range (2.13 or more).

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  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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EP16772782.5A 2015-03-30 2016-03-29 Matériau de fil d'acier à haute teneur en carbone présentant une excellente aptitude à l'étirage de fil et fil d'acier Active EP3282027B1 (fr)

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TWI658472B (zh) * 2017-04-28 2019-05-01 吳政雄 複合導電體結合之電導體及其製造方法
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CN113293337A (zh) * 2021-04-28 2021-08-24 顿口渔具科技(东莞)有限公司 一种鱼钩用铌-钒复合微合金化高碳钢丝
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JP4016894B2 (ja) * 2003-06-12 2007-12-05 住友金属工業株式会社 鋼線材及び鋼線の製造方法
JP4621133B2 (ja) * 2004-12-22 2011-01-26 株式会社神戸製鋼所 伸線性に優れた高炭素鋼線材およびその製法
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JP2007327084A (ja) * 2006-06-06 2007-12-20 Kobe Steel Ltd 伸線加工性に優れた線材およびその製造方法
JP4970562B2 (ja) * 2009-04-21 2012-07-11 新日本製鐵株式会社 延性に優れた高強度鋼線用線材及び鋼線の製造方法
MX2011008034A (es) * 2010-02-01 2011-10-05 Nippon Steel Corp Varilla de alambre, alambre de acero, y metodo de fabricacion de los mismos.
BR112012025089A2 (pt) * 2010-04-01 2017-09-12 Kobe Steel Ltd Fio de aço de alto carbono excelente na estampabilidade de fio e propriedade de fadiga após trefilagem do fio
US20120318410A1 (en) * 2010-04-08 2012-12-20 Toshimi Tarui Strand for saw wire and manufacturing method thereof
JP5802162B2 (ja) * 2012-03-29 2015-10-28 株式会社神戸製鋼所 線材及びこれを用いた鋼線

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US20180087125A1 (en) 2018-03-29
WO2016158901A1 (fr) 2016-10-06
EP3282027A4 (fr) 2018-09-05
EP3282027B1 (fr) 2020-10-21
CN107406950A (zh) 2017-11-28
CA2980886C (fr) 2019-09-24
KR20170130527A (ko) 2017-11-28
ES2835325T3 (es) 2021-06-22
CA2980886A1 (fr) 2016-10-06
CN107406950B (zh) 2020-04-14
JP6795319B2 (ja) 2020-12-02

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