WO2012093715A1 - 鋼線材及びその製造方法 - Google Patents

鋼線材及びその製造方法 Download PDF

Info

Publication number
WO2012093715A1
WO2012093715A1 PCT/JP2012/050155 JP2012050155W WO2012093715A1 WO 2012093715 A1 WO2012093715 A1 WO 2012093715A1 JP 2012050155 W JP2012050155 W JP 2012050155W WO 2012093715 A1 WO2012093715 A1 WO 2012093715A1
Authority
WO
WIPO (PCT)
Prior art keywords
less
scale
amount
steel wire
excluding
Prior art date
Application number
PCT/JP2012/050155
Other languages
English (en)
French (fr)
Japanese (ja)
Inventor
武田　実佳子
昌平 中久保
和彦 桐原
雅之 遠藤
Original Assignee
株式会社神戸製鋼所
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 株式会社神戸製鋼所 filed Critical 株式会社神戸製鋼所
Priority to US13/995,739 priority Critical patent/US20130272914A1/en
Priority to CN201280004664.4A priority patent/CN103314125B/zh
Priority to KR1020137017580A priority patent/KR20130087613A/ko
Priority to EP12732406.9A priority patent/EP2662468A4/de
Priority to KR1020147014715A priority patent/KR20140076642A/ko
Publication of WO2012093715A1 publication Critical patent/WO2012093715A1/ja

Links

Images

Classifications

    • 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
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/16—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling wire rods, bars, merchant bars, rounds wire or material of like small cross-section
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C21D1/76—Adjusting the composition of the atmosphere
    • 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
    • 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
    • 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
    • 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
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/561—Continuous furnaces for strip or wire with a controlled atmosphere or vacuum
    • 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
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/562—Details
    • 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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—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
    • C22C38/12—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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/32—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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • D—TEXTILES; PAPER
    • D07—ROPES; CABLES OTHER THAN ELECTRIC
    • D07B—ROPES OR CABLES IN GENERAL
    • D07B1/00—Constructional features of ropes or cables
    • D07B1/06—Ropes or cables built-up from metal wires, e.g. of section wires around a hemp core
    • D07B1/0606—Reinforcing cords for rubber or plastic articles
    • D07B1/066—Reinforcing cords for rubber or plastic articles the wires being made from special alloy or special steel composition
    • D—TEXTILES; PAPER
    • D07—ROPES; CABLES OTHER THAN ELECTRIC
    • D07B—ROPES OR CABLES IN GENERAL
    • D07B2205/00—Rope or cable materials
    • D07B2205/30—Inorganic materials
    • D07B2205/3021—Metals
    • D07B2205/3025—Steel

Definitions

  • the present invention relates to a steel wire and a method for producing the same, and in particular, a hot-rolled steel wire formed with a thin scale that can be easily removed by mechanical descaling without being peeled off during cooling after hot rolling or during storage and transportation. (Hereinafter simply referred to as “wire”) and its manufacturing method.
  • a scale is usually formed on the surface of the wire manufactured by hot rolling, and it is necessary to remove this scale before subjecting the wire to secondary processing such as wire drawing.
  • a method for removing scale before such secondary processing a batch-type pickling method has been used in the past, but in recent years, from the viewpoint of pollution problems and cost reduction, a mechanical descaling (hereinafter referred to as MD) method is used. Is being used. Therefore, it is requested
  • Patent Documents 1 to 5 can be cited as methods for producing a wire having a scale with good MD properties.
  • the scale amount remaining in the wire after MD is reduced by forming a thick scale with a high FeO ratio.
  • Patent Literature 3 by reducing the interface roughness, the propagation of cracks generated at the scale interface is promoted, and the residual scale amount is reduced.
  • Patent Documents 4 and 5 the peelability of the scale is improved by controlling the area ratio of the pores in the scale.
  • Patent Documents 1 to 5 described above have the following problems.
  • the yield is lowered, and the scale is peeled off during the cooling process, storage and transportation, and rust is generated.
  • the scale is thick, it is difficult to completely remove the scale even if bending strain is applied to the wire by the MD method and further the surface of the wire is brushed. That is, unlike the batch type pickling method, the MD method is difficult to remove the entire scale uniformly and stably, and even if MD is applied to a wire having a thick scale, the surface of the wire In some cases, finely crushed scale powder is scattered. In this way, when the residual scale remaining locally increases, problems such as wrinkles due to poor lubrication and a decrease in the die life may occur in secondary processing such as wire drawing.
  • Patent Documents 1 to 5 do not consider any scale peeling due to the compressive stress generated during cooling, and the scale peels during cooling, storage, or transportation, and rust is generated on the wire before MD. There was a problem to do.
  • the present invention has been made in view of the above circumstances, and the purpose thereof is a wire rod formed with a scale that does not peel off during cooling after hot rolling or during storage / transport, but easily peels off during MD, And a manufacturing method thereof.
  • the steel wire rod according to the present invention that has achieved the above-mentioned problems is: C: 0.05 to 1.2% (meaning mass%, hereinafter the same for chemical components), Si: 0.01 to 0.5%, Mn: 0.1 to 1.5%, P: 0.02% or less (not including 0%), S: 0.02% or less (not including 0%), N: 0.005% or less (0% Steel wire with the balance being iron and inevitable impurities, the scale having a thickness of 7.0 ⁇ m or less, and the FeO ratio in the scale being 30 to 80% by volume, Fe 2 SiO 4 ratio is less than 0.1% by volume.
  • the steel wire rod according to the present invention includes (a) Cr: 0.3% or less (not including 0%) and / or Ni: 0.3% or less (not including 0%), (b) Cu as required. : 0.2% or less (excluding 0%), (c) at least one element selected from the group consisting of Nb, V, Ti, Hf, and Zr is 0.1% or less in total (0 %), (D) Al: 0.1% or less (not including 0%), (e) B: 0.005% or less (not including 0%), (f) Ca: 0.01 % Or less (not including 0%) and / or Mg: 0.01% or less (not including 0%) may be contained.
  • the present invention provides a mixed gas of oxygen and an inert gas in which the steel having any one of the chemical components described above is rolled up at 750 to 880 ° C. after hot rolling and the oxygen fraction is less than 20% by volume, Or the manufacturing method of the steel wire which cools, spraying an inert gas is also included.
  • the inert gas is preferably nitrogen.
  • the wire rod of the present invention has a thin (7.0 ⁇ m or less) scale in which the FeO ratio is appropriately controlled (30 to 80% by volume) within a predetermined range. Therefore, the scale does not peel off during cooling after hot rolling or during storage / transport, and rusting can be prevented. Furthermore, according to the present invention, since the scale is easily peeled off at the time of MD, sufficient peelability can be ensured with a simple descaling device, and adverse effects during secondary processing such as wire drawing (the surface of the wire surface due to leftover of the scale, It is possible to provide a high quality steel wire rod without causing poor lubrication. Further, since the scale loss is small, the yield can be maintained high.
  • FIG. 1 is a graph showing the relationship between the FeO ratio in the scale and the residual scale area ratio after MD.
  • FIG. 2 is a graph showing the relationship between the scale thickness and the scale peeling rate of the rolled material.
  • the MD method is a method in which a wire is distorted to cause cracks in the scale or at the interface between the ground iron and the scale, and the scale is peeled off.
  • the ratio of FeO in the scale has been improved. This is because the adhesion strength of FeO to the ground iron is smaller than that of Fe 2 O 3 or Fe 3 O 4 , so increasing the FeO ratio in the scale is effective in improving the scale peelability during MD. Because it is considered.
  • a thick scale peels off during the cooling process, storage and transportation. That is, it was extremely difficult to reduce the thickness of the scale and to secure the FeO ratio in the scale.
  • the coiling temperature after hot rolling is set to a relatively low temperature, and then cooling while injecting a mixed gas or inert gas of oxygen and inert gas having a low oxygen fraction.
  • the scale can be thinned and the FeO ratio in the scale can be secured at a predetermined level or more.
  • the scale thickness is preferably 6.5 ⁇ m or less, more preferably 6.0 ⁇ m or less (particularly 5.5 ⁇ m or less).
  • the lower limit of the scale thickness is not particularly limited, but is usually about 0.9 ⁇ m.
  • FIG. 1 is a graph showing the relationship between the FeO ratio in the scale and the area ratio of the scale remaining after MD.
  • FIG. 1 shows that if the FeO ratio in the scale is 30 to 80% by volume, the amount of residual scale after MD can be sufficiently reduced.
  • the FeO ratio is preferably 35% by volume or more and 75% by volume or less, more preferably 40% by volume or more and 70% by volume or less, and further preferably 45% by volume or more and 65% by volume or less.
  • the proportion of Fe 2 SiO 4 (firelite) in the scale is less than 0.1% by volume.
  • Fe 2 SiO 4 is generated excessively, it is generated non-uniformly at the interface between the scale and the ground iron, and the scale is exfoliated unevenly during MD, so that the MD property deteriorates.
  • the Fe 2 SiO 4 ratio is preferably 0.09% by volume or less, more preferably 0.08% by volume or less, and still more preferably 0.07% by volume or less.
  • Fe 2 SiO 4 in the scale is an oxide that is brittle and easily peeled off, and if it is a trace amount, it is uniformly thinly formed, so that it has an effect of improving MD properties. In order to effectively exhibit such an action, it is preferable to ensure 0.01% by volume or more, more preferably 0.02% by volume or more, and further preferably 0.03% by volume or more.
  • the scale in the present invention includes Fe 2 O 3 , Fe 3 O 4 and the like in addition to FeO and Fe 2 SiO 4 .
  • the amount of residual scale after MD can be reduced to 30% or less in terms of the area ratio with respect to the amount of scale before MD. This corresponds to approximately 0.05% by mass or less in the remaining scale amount with respect to the mass of the steel wire.
  • the residual scale amount is preferably 25 area% or less, more preferably 20 area% or less.
  • a steel having the chemical composition described later is hot-rolled, wound at a relatively low temperature (750 to 880 ° C.), and then mixed with oxygen and an inert gas having a low oxygen fraction. It is important to cool while spraying gas or inert gas.
  • the scale can be thinned by winding at a low temperature. Further, by blowing and cooling a gas having a low oxygen fraction or containing no oxygen as described above, the generated FeO can be secured at a predetermined level or more without changing to Fe 3 O 4 .
  • the coiling temperature after hot rolling exceeds 880 ° C.
  • the scale thickness exceeds 7.0 ⁇ m
  • the FeO ratio in the scale exceeds 80% by volume
  • the MD property deteriorates.
  • the coiling temperature exceeds 880 ° C., it may exceed 0.1% by volume, and Fe 2 SiO 4 (firelight) is generated unevenly at the interface between the scale and the ground iron. Unevenly peels off and MD properties deteriorate.
  • the coiling temperature is lower than 750 ° C., the FeO ratio cannot be ensured by 30% by volume or more, and the MD property deteriorates.
  • the winding temperature is preferably 770 ° C. or higher and 875 ° C. or lower, more preferably 790 ° C. or higher and 860 ° C. or lower.
  • Cooling after hot rolling is performed while spraying a mixed gas of oxygen and an inert gas having an oxygen fraction of less than 20% by volume, or an inert gas.
  • the oxygen fraction is preferably 10% by volume or less, more preferably 5% by volume or less, and still more preferably 0% by volume (that is, only inert gas).
  • the inert gas include argon, nitrogen and the like, preferably nitrogen.
  • the cooling stop temperature of the cooling performed by spraying the gas is not particularly limited. For example, the cooling may be performed while spraying the gas up to about 550 to 650 ° C., and then cooling to room temperature in the atmosphere.
  • C 0.05 to 1.2% C is an element that greatly affects the mechanical properties of steel.
  • the C content was set to 0.05% or more.
  • the amount of C is preferably 0.15% or more, and more preferably 0.3% or more.
  • the C amount is set to 1.2% or less.
  • the amount of C is preferably 1.1% or less, and more preferably 1.0% or less.
  • Si 0.01 to 0.5% Si is an element necessary for deoxidation of steel, and if its content is too small, the production of Fe 2 SiO 4 (firelight) becomes insufficient and the MD property deteriorates. Therefore, the Si amount is determined to be 0.01% or more.
  • the amount of Si is preferably 0.1% or more, and more preferably 0.2% or more.
  • the Si amount is set to 0.5% or less.
  • the amount of Si is preferably 0.45% or less, and more preferably 0.4% or less.
  • Mn 0.1 to 1.5% Mn is an element useful for securing the hardenability of steel and increasing the strength. In order to effectively exhibit such an action, the amount of Mn was determined to be 0.1% or more. The amount of Mn is preferably 0.2% or more, and more preferably 0.4% or more. On the other hand, when the amount of Mn is excessive, segregation occurs in the cooling process after hot rolling, and a supercooled structure (such as martensite) that is harmful to wire drawing workability is likely to occur. Therefore, the amount of Mn is set to 1.5% or less. The amount of Mn is preferably 1.4% or less, more preferably 1.2% or less.
  • P 0.02% or less (excluding 0%)
  • P is an element that deteriorates the toughness and ductility of steel.
  • the P content is set to 0.02% or less.
  • the amount of P is preferably 0.01% or less, and more preferably 0.005% or less.
  • the lower limit of the amount of P is not particularly limited, but is usually about 0.001%.
  • S 0.02% or less (excluding 0%) S, like P, is an element that degrades the toughness and ductility of steel. In order to prevent disconnection in the wire drawing or the subsequent twisting process, the S content is set to 0.02% or less.
  • the amount of S is preferably 0.01% or less, and more preferably 0.005% or less.
  • the lower limit of the amount of S is not particularly limited, but is usually about 0.001%.
  • N 0.005% or less (excluding 0%)
  • N is an element that deteriorates the ductility of steel when the content is excessive. Therefore, the N amount is set to 0.005% or less.
  • the amount of N is preferably 0.004% or less, and more preferably 0.003% or less.
  • the lower limit of the N amount is not particularly limited, but is usually about 0.001%.
  • the basic components of the steel wire rod of the present invention are as described above, and the balance is substantially iron. However, it is naturally allowed that the inevitable impurities brought in depending on the situation of raw materials, materials, manufacturing facilities, etc. are included in the steel wire. Furthermore, it is also recommended to add the following elements as necessary within a range not impeding the effects of the present invention.
  • Cr 0.3% or less (not including 0%) and / or Ni: 0.3% or less (not including 0%) Cr and Ni are both elements that increase the hardenability of steel and contribute to the improvement of strength.
  • the Cr content is preferably 0.05% or more, and the Ni content is preferably 0.03% or more. More preferably, the Cr amount and the Ni amount are both 0.10% or more, and more preferably both are 0.12% or more.
  • the Cr content and the Ni content are both 0.3% or less. More preferably, the Cr content and the Ni content are both 0.25% or less, more preferably 0.20% or less.
  • Cu 0.2% or less (excluding 0%) Cu is an element having an action of promoting scale peeling.
  • the amount of Cu is preferably 0.01% or more.
  • the amount of Cu is more preferably 0.05% or more, and further preferably 0.10% or more.
  • the amount of Cu becomes excessive, peeling of the scale is excessively promoted, the scale is peeled off during rolling, and another thin scale with high adhesion is generated on the peeled surface, and the wire coil is stored and transported. Rust is generated when Therefore, the amount of Cu is preferably 0.2% or less.
  • the amount of Cu is more preferably 0.17% or less, and still more preferably 0.15% or less.
  • Nb, V, Ti, Hf, and Zr are all elements that form fine carbonitrides and contribute to high strength.
  • the Nb amount, the V amount, the Ti amount, the Hf amount, and the Zr amount are all 0.003% or more.
  • the Nb amount, V amount, Ti amount, Hf amount, and Zr amount are all preferably 0.007% or more, and more preferably 0.01% or more.
  • the total amount of these elements is preferably 0.1% or less.
  • the total amount of these elements is more preferably 0.08% or less, still more preferably 0.06% or less.
  • Al 0.1% or less (excluding 0%) Al is an element effective as a deoxidizer.
  • the Al content is preferably 0.001% or more.
  • the amount of Al is more preferably 0.005% or more, and still more preferably 0.01% or more.
  • the Al content is preferably 0.1% or less.
  • the amount of Al is more preferably 0.08% or less, and still more preferably 0.06% or less.
  • B 0.005% or less (excluding 0%)
  • B is an element that suppresses the formation of ferrite by being present as free B that dissolves in steel (B that does not form a compound), and is particularly effective for high-strength wires that require suppression of longitudinal cracks. It is.
  • the B content is preferably 0.0001% or more.
  • the amount of B is more preferably 0.0005% or more, and further preferably 0.0010% or more.
  • the B content is preferably 0.005% or less, more preferably 0.0040% or less, and still more preferably 0.0035% or less.
  • Ca and Mg are both elements that have the effect of increasing the ductility by controlling the form of inclusions. Moreover, Ca also has the effect
  • both the Ca content and the Mg content are preferably 0.001% or more.
  • Ca and Mg are both preferably 0.002% or more, and more preferably 0.003% or more.
  • both the Ca content and the Mg content are preferably 0.01% or less.
  • the Ca content and the Mg content are both preferably 0.008% or less, and more preferably 0.005% or less.
  • the obtained steel wire was measured by the following method.
  • No. 3, 29, 33, 36, 40, 43, 46, 47, and 49 have deteriorated MD properties because the manufacturing conditions do not satisfy the requirements of the present invention.
  • No. 3, 29, 36, 40, 43, 46, and 47 are examples in which air was blown and cooled after hot rolling, and FeO became Fe 3 O 4 during cooling, so that the FeO fraction was It could not be secured, and the MD property deteriorated.
  • No. No. 33 is an example in which the coiling temperature after hot rolling was high. The scale thickness was increased, the FeO ratio was too large, and the Fe 2 SiO 4 ratio was also high, so the MD property deteriorated.
  • No. Nos. 50 to 54 are examples in which the coiling temperature after hot rolling was higher, the scale thickness exceeded 7.0 ⁇ m, the scale peeling rate of the rolled material increased, and rust was generated. That is, no. Nos. 50 to 54 are considered to cause rust due to dropping of the scale during cooling after hot rolling or during storage and transportation.
  • FIG. 2 shows the relationship between the scale thickness and the scale peeling rate of the rolled material. It can be seen that when the scale thickness exceeds 7.0 ⁇ m, the scale peeling rate of the rolled material increases.
  • the steel wire rod of the present invention is excellent in mechanical descaling after hot rolling (before wire drawing), it cuts automobile tire cords (steel cords, bead wires), hose wires, semiconductor silicon, etc. It is useful as a material such as saw wire used in

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
PCT/JP2012/050155 2011-01-07 2012-01-06 鋼線材及びその製造方法 WO2012093715A1 (ja)

Priority Applications (5)

Application Number Priority Date Filing Date Title
US13/995,739 US20130272914A1 (en) 2011-01-07 2012-01-06 Steel wire material and method for manufacturing same
CN201280004664.4A CN103314125B (zh) 2011-01-07 2012-01-06 钢线材及其制造方法
KR1020137017580A KR20130087613A (ko) 2011-01-07 2012-01-06 강선재 및 그 제조 방법
EP12732406.9A EP2662468A4 (de) 2011-01-07 2012-01-06 Stahldrahtmaterial und herstellungsverfahren dafür
KR1020147014715A KR20140076642A (ko) 2011-01-07 2012-01-06 강선재의 제조 방법

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2011002014A JP4980471B1 (ja) 2011-01-07 2011-01-07 鋼線材及びその製造方法
JP2011-002014 2011-01-07

Publications (1)

Publication Number Publication Date
WO2012093715A1 true WO2012093715A1 (ja) 2012-07-12

Family

ID=46457565

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2012/050155 WO2012093715A1 (ja) 2011-01-07 2012-01-06 鋼線材及びその製造方法

Country Status (6)

Country Link
US (1) US20130272914A1 (de)
EP (1) EP2662468A4 (de)
JP (1) JP4980471B1 (de)
KR (2) KR20140076642A (de)
CN (1) CN103314125B (de)
WO (1) WO2012093715A1 (de)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2018194038A1 (ja) * 2017-04-17 2018-10-25 株式会社ブリヂストン ケーブルビードおよびこれを用いた航空機用タイヤ

Families Citing this family (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105088063B (zh) * 2014-05-19 2017-04-26 上海梅山钢铁股份有限公司 一种加工硬化高强钢及其制造方法
CN105316573B (zh) * 2014-06-23 2017-07-21 鞍钢股份有限公司 一种适于酸洗除鳞的80级帘线钢盘条及其生产方法
CN106661649B (zh) * 2014-10-08 2019-05-03 新日铁住金株式会社 具有高强度和优异的化学转化处理性的热处理钢制品及其制造方法
BR112017020004A2 (pt) * 2015-04-08 2018-06-19 Nippon Steel & Sumitomo Metal Corporation folha de aço para tratamento térmico
MX2017012873A (es) 2015-04-08 2018-01-15 Nippon Steel & Sumitomo Metal Corp Miembro de lamina de acero con tratamiento termico y metodo para producirlo.
CA2982087C (en) 2015-04-08 2020-01-21 Nippon Steel & Sumitomo Metal Corporation Heat-treated steel sheet member and method for producing the same
KR101676201B1 (ko) * 2015-12-07 2016-11-15 주식회사 포스코 수소유기균열 저항성이 우수한 고탄소강 선재, 강선 및 이들의 제조방법
JP6757194B2 (ja) * 2016-07-11 2020-09-16 日本パーカライジング株式会社 スケール除去性に優れた熱処理前炭素鋼材、熱処理後炭素鋼材及びそれらの製造方法、並びに、スケール除去方法及び易脱スケール性皮膜形成用剤
JP6865273B2 (ja) 2017-04-28 2021-04-28 株式会社ブリヂストン ゴム物品補強用スチールコード、その製造方法及びタイヤ
WO2020065372A1 (en) * 2018-09-25 2020-04-02 Arcelormittal High strength hot rolled steel having excellent scale adhesivness and a method of manufacturing the same
DK3674425T3 (en) * 2018-12-31 2022-05-23 Baker Hughes Energy Tech Uk Limited Stålwire
CN110560495A (zh) * 2019-09-17 2019-12-13 安徽工业大学 一种实验室用除鳞实验平台及其实验方法

Citations (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04293721A (ja) 1991-03-22 1992-10-19 Nippon Steel Corp メカニカルデスケーリング性に優れた軟鋼線材の製造法
JPH07331384A (ja) * 1994-06-03 1995-12-19 Nippon Steel Corp メカニカルデスケーリング性と生引き性に優れた線材
JPH08295992A (ja) 1995-04-21 1996-11-12 Nippon Steel Corp デスケーリング用線材
JPH10324923A (ja) 1997-05-27 1998-12-08 Nippon Steel Corp 鋼線用線材
JPH11172332A (ja) 1997-12-15 1999-06-29 Sumitomo Metal Ind Ltd 高炭素鋼線材
JP2000246322A (ja) * 1999-02-25 2000-09-12 Kobe Steel Ltd 酸洗性に優れた圧延線材およびその製造方法
JP2001032042A (ja) * 1999-07-19 2001-02-06 Kobe Steel Ltd メカニカルデスケーリング時のスケール剥離性に優れた鋼線材
JP2001071019A (ja) * 1999-09-09 2001-03-21 Nkk Corp スケール密着性に優れた高炭素熱延鋼板の製造方法
JP2005281793A (ja) * 2004-03-30 2005-10-13 Sumitomo Metal Ind Ltd 鋼線用線材の製造方法及び鋼線用線材
JP2006028619A (ja) 2004-07-21 2006-02-02 Sumitomo Metal Ind Ltd 高強度低合金鋼線材
JP2007070728A (ja) * 2005-08-12 2007-03-22 Kobe Steel Ltd メカニカルデスケーリング性に優れた鋼線材およびその製造方法
JP2008049391A (ja) * 2006-08-28 2008-03-06 Kobe Steel Ltd スケール剥離性に優れた鋼材の製造方法。
JP2008069376A (ja) * 2006-09-12 2008-03-27 Kobe Steel Ltd 伸線性に優れた鋼線材およびその製造方法

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1921172B1 (de) * 2005-08-12 2012-11-28 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Verfahren zur herstellung von stahlmaterial mit hervorragender zunderablösungseigenschaft und stahldrahtmaterial mit hervorragender zunderablösungseigenschaft

Patent Citations (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04293721A (ja) 1991-03-22 1992-10-19 Nippon Steel Corp メカニカルデスケーリング性に優れた軟鋼線材の製造法
JPH07331384A (ja) * 1994-06-03 1995-12-19 Nippon Steel Corp メカニカルデスケーリング性と生引き性に優れた線材
JPH08295992A (ja) 1995-04-21 1996-11-12 Nippon Steel Corp デスケーリング用線材
JPH10324923A (ja) 1997-05-27 1998-12-08 Nippon Steel Corp 鋼線用線材
JPH11172332A (ja) 1997-12-15 1999-06-29 Sumitomo Metal Ind Ltd 高炭素鋼線材
JP2000246322A (ja) * 1999-02-25 2000-09-12 Kobe Steel Ltd 酸洗性に優れた圧延線材およびその製造方法
JP2001032042A (ja) * 1999-07-19 2001-02-06 Kobe Steel Ltd メカニカルデスケーリング時のスケール剥離性に優れた鋼線材
JP2001071019A (ja) * 1999-09-09 2001-03-21 Nkk Corp スケール密着性に優れた高炭素熱延鋼板の製造方法
JP2005281793A (ja) * 2004-03-30 2005-10-13 Sumitomo Metal Ind Ltd 鋼線用線材の製造方法及び鋼線用線材
JP2006028619A (ja) 2004-07-21 2006-02-02 Sumitomo Metal Ind Ltd 高強度低合金鋼線材
JP2007070728A (ja) * 2005-08-12 2007-03-22 Kobe Steel Ltd メカニカルデスケーリング性に優れた鋼線材およびその製造方法
JP2008049391A (ja) * 2006-08-28 2008-03-06 Kobe Steel Ltd スケール剥離性に優れた鋼材の製造方法。
JP2008069376A (ja) * 2006-09-12 2008-03-27 Kobe Steel Ltd 伸線性に優れた鋼線材およびその製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP2662468A4

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2018194038A1 (ja) * 2017-04-17 2018-10-25 株式会社ブリヂストン ケーブルビードおよびこれを用いた航空機用タイヤ

Also Published As

Publication number Publication date
KR20130087613A (ko) 2013-08-06
CN103314125B (zh) 2015-05-27
CN103314125A (zh) 2013-09-18
EP2662468A1 (de) 2013-11-13
KR20140076642A (ko) 2014-06-20
JP4980471B1 (ja) 2012-07-18
JP2012144756A (ja) 2012-08-02
US20130272914A1 (en) 2013-10-17
EP2662468A4 (de) 2015-05-27

Similar Documents

Publication Publication Date Title
JP4980471B1 (ja) 鋼線材及びその製造方法
JP4958998B1 (ja) 鋼線材及びその製造方法
KR101103233B1 (ko) 강선재
JP5179331B2 (ja) 伸線加工性およびメカニカルデスケーリング性に優れた熱間圧延線材およびその製造方法
KR101699194B1 (ko) 무방향성 전기 강판 제조용의 열연 강판 및 그 제조 방법
TWI665313B (zh) 無方向性電磁鋼板及其製造方法
EP1921172B1 (de) Verfahren zur herstellung von stahlmaterial mit hervorragender zunderablösungseigenschaft und stahldrahtmaterial mit hervorragender zunderablösungseigenschaft
JP6127440B2 (ja) 無方向性電磁鋼板製造用の熱延鋼板およびその製造方法
WO2011055746A1 (ja) 加工性に優れた高炭素鋼線材
KR101870063B1 (ko) 고강도 스틸 코드용 필라멘트
EP3366802A1 (de) Stahldraht zum drahtziehen
WO2003066923A1 (fr) Fil d'acier possedant une excellente caracteristique de decalaminage en decalaminage mecanique et son procede de production
JP5297849B2 (ja) 伸線性に優れた高炭素鋼線材の製造方法
CN112840044A (zh) 热轧线材
JP2007070728A (ja) メカニカルデスケーリング性に優れた鋼線材およびその製造方法
JP2007217790A (ja) 鋼線材
JP4971720B2 (ja) メカニカルデスケーリング用鋼線材

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 12732406

Country of ref document: EP

Kind code of ref document: A1

WWE Wipo information: entry into national phase

Ref document number: 13995739

Country of ref document: US

WWE Wipo information: entry into national phase

Ref document number: 2012732406

Country of ref document: EP

ENP Entry into the national phase

Ref document number: 20137017580

Country of ref document: KR

Kind code of ref document: A

WWE Wipo information: entry into national phase

Ref document number: 1301003787

Country of ref document: TH

NENP Non-entry into the national phase

Ref country code: DE