EP2662468A1 - Stahldrahtmaterial und herstellungsverfahren dafür - Google Patents

Stahldrahtmaterial und herstellungsverfahren dafür Download PDF

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Publication number
EP2662468A1
EP2662468A1 EP20120732406 EP12732406A EP2662468A1 EP 2662468 A1 EP2662468 A1 EP 2662468A1 EP 20120732406 EP20120732406 EP 20120732406 EP 12732406 A EP12732406 A EP 12732406A EP 2662468 A1 EP2662468 A1 EP 2662468A1
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Prior art keywords
less
scale
wire material
amount
vol
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EP20120732406
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English (en)
French (fr)
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EP2662468A4 (de
Inventor
Mikako Takeda
Shohei Nakakubo
Kazuhiko Kirihara
Masayuki Endo
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Kobe Steel Ltd
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Kobe Steel Ltd
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    • 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
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
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    • 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
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    • 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 material and a method for manufacturing the same, and relates more specifically to a hot rolled steel wire material (hereinafter simply referred to as "wire material") formed with a thin scale not peeling off during cooling after hot rolling and at the time of storage and transportation and easily removable by mechanical descaling, and a method for manufacturing the same.
  • wire material a hot rolled steel wire material
  • a scale is formed normally on the surface of a wire material manufactured by hot rolling, and it is required to remove the scale before subjecting the wire material to secondary work such as drawing and the like.
  • a scale removing method before secondary work a batch type acid cleaning method was employed in prior arts, however, in recent years, from the viewpoints of the environmental pollution and cost reduction, a mechanical descaling (hereinafter referred to as MD) method has come to be employed. Therefore, the wire material is required to be formed with a scale with excellent MD performance.
  • Patent Literatures 1-5 can be cited for example.
  • the scale amount remaining in the wire material after MD is reduced by forming a scale which is high in FeO ratio and thick.
  • Patent Literature 3 by lowering the boundary face roughness, propagation of the crack occurring on the boundary face of the scale is promoted, and the remaining scale amount is reduced.
  • Patent Literatures 1-5 described above have problems as described below. According to the method of forming the scale thick as Patent Literatures 1, 2, drop of the yield is caused, the scale peels off during the cooling step and at the time of storage and transportation, and the rust is generated. Also, when the scale is thick, even when a bending strain is applied to the wire material by the MD method and the wire material surface is subjected to brushing, it is difficult to perfectly remove the scale. More specifically, according to the MD method, unlike the batch type acid cleaning method, it is difficult to remove the entire scale evenly and stably, and even when the wire material formed with thick scale is subjected to MD, the surface of the wire material may occasionally be spotted with finely crushed scale powder. When the remaining scale remaining locally thus increases, in the secondary work such as drawing and the like, problems such as occurrence of a flaw due to the defective lubrication, lowering of the lifetime of the dice and the like are caused.
  • the present invention has been developed in view of the circumstances described above, and its object is to provide a wire material formed with a scale not peeling off during cooling after hot rolling and at the time of storage and transportation and easily peeling off at the time of MD, and a method for manufacturing the same.
  • the steel wire material of the present invention which solved the problems described above is a steel wire material containing C: 0.05-1.2% ("%” means “% by mass”, hereinafter the same for chemical components), Si: 0.01-0.5%, Mn: 0.1-1.5%, P: 0.02% or less (not including 0%), S: 0.02% or less (not including 0%), and N: 0.005% or less (not including 0%), with the remainder being iron and unavoidable impurities, in which a scale with 7.0 ⁇ m or less thickness is included, FeO ratio inside the scale is 30-80 vol%, and Fe 2 SiO 4 ratio is less than 0.1 vol%.
  • the steel wire material of the present invention may also contain (a) Cr: 0.3% or less (not including 0%) and/or Ni: 0.3% or less (not including 0%), (b) Cu: 0.2% or less (not including 0%), (c) at least one element selected from a group consisting of Nb, V, Ti, Hf and Zr by 0.1% or less (not including 0%) in total, (d) Al: 0.1% or less (not including 0%), (e) B: 0.005% or less (not including 0%), and (f) Ca: 0.01% or less (not including 0%) and/or Mg: 0.01% or less (not including 0%).
  • the present invention also includes a method for manufacturing a steel wire material including a step of hot rolling steel of any of the chemical compositions described above, a step of thereafter winding up the hot rolled steel at 750-880°C, and a step of cooling the wound steel while injecting a gas mixture of oxygen and an inert gas whose oxygen fraction is less than 20 vol% or an inert gas. It is preferable that the inert gas is nitrogen.
  • the FeO ratio is appropriately controlled to a predetermined range (30-80 vol%), and a thin (7 ⁇ m or less) scale is included. Accordingly, the scale does not peel off during cooling after hot rolling and at the time of storage and transportation, and generation of the rust can be prevented. Further, according to the present invention, because the scale easily peels off at the time of MD, sufficient peeling performance can be secured with a simple descaling device, adverse effects (a flaw on the surface of the wire material, defective lubrication and the like due to leaving the scale unremoved) are not exerted in secondary work such as drawing and the like, and the steel wire material of high quality can be provided. Also, because the scale loss is less, high yield can be maintained.
  • a compression stress is generated inside the scale due to the difference in the coefficient of thermal expansion between the base iron and the scale.
  • the scale naturally peels off during the cooling step or at the time of storage and transportation of the wire material thereafter, which became the cause of generation of the rust.
  • the scale is removed by MD before executing secondary work such as drawing and the like, and the lifetime of the dice is shortened when the scale remains after MD. Therefore, the wire material having a scale that does not peel off in the cooling step during the manufacturing process and at the time of storage and transportation and easily peels off at the time of MD has been desired.
  • the MD method is a method for making the scale peel off by applying strain to the wire material to generate cracks inside the scale or in the boundary face of the base iron and the scale.
  • increase of the FeO ratio inside the scale has been executed in order to improve the peeling performance of the scale. This is because the increase of the FeO ratio inside the scale is considered to be effective in improving the peeling performance of the scale at the time of MD because the strength of FeO is weaker than Fe 2 O 3 and Fe 3 O 4 .
  • the scale thickness is preferably 6.5 ⁇ m or less, more preferably 6.0 ⁇ m or less (particularly 5.5 ⁇ m or less). Although the lower limit of the scale thickness is not particularly limited, it is approximately 0.9 ⁇ m normally.
  • the present inventors investigated the relation between the FeO ratio inside the scale and the MD performance. More specifically, the wire material with 200 mm length having a composition of 0.9% C-0.25% Si-0.86% Mn-0.007% P-0.0063% S-0.002% N was used, the winding temperature condition was changed, and the samples whose composition of the scale was adjusted were manufactured. Also, the winding temperature was changed in the range of 700-1,000°C, and N 2 -10 vol% O 2 gas was used for cooling after winding. The scale was made peel off by applying a deformation strain (6%) equivalent to MD to the manufactured sample, and the scale amount (area ratio) remained was measured by image analysis similarly to the example described below.
  • Fig. 1 is a graph showing the relation between the FeO ratio inside the scale and the area ratio of the scale that remained after MD.
  • the FeO ratio is preferably 35 vol% or more and 75 vol% or less, more preferably 40 vol% or more and 70 vol% or less, and further more preferably 45 vol% or more and 65 vol% or less.
  • the Fe 2 SiO 4 (fayalite) ratio inside the scale is to be less than 0.1 vol%.
  • the Fe 2 SiO 4 ratio is preferably 0.09 vol% or less, more preferably 0.08 vol% or less, and further more preferably 0.07 vol% or less.
  • Fe 2 SiO 4 inside the scale is an oxide that is brittle and easily peels off and is formed evenly and thin if its amount is slight, it has an action of improving the MD performance. In order to exert such action effectively, it is preferable to secure Fe 2 SiO 4 by 0.01 vol% or more, more preferably 0.02 vol% or more, and further more preferably 0.03 vol% or more.
  • Fe 2 O 3, Fe 3 O 4 and the like are included other than FeO and Fe 2 SiO 4 .
  • the remaining scale amount after MD can be made 30% or less by the area ratio relative to the scale amount before MD. This is equivalent to approximately 0.05 mass% or less in terms of the remaining scale amount relative to the mass of the steel wire material.
  • the remaining scale amount is preferably 25% or less by area, more preferably 20% or less by area.
  • the winding temperature after hot rolling exceeds 880°C
  • the scale thickness exceeds 7.0 ⁇ m
  • the FeO ratio inside the scale exceeds 80 vol%
  • the MD performance deteriorates.
  • Fe 2 SiO 4 possibly exceeds 0.1 vol% and is formed unevenly on the boundary surface between the scale and the base iron
  • the scale peels off unevenly at the time of MD, and the MD performance deteriorates.
  • the winding temperature is below 750°C, 30 vol% or more of the FeO ratio cannot be secured, and the MD performance deteriorates.
  • the winding temperature is preferably 770°C or above and 875°C or below, more preferably 790°C or above and 860°C or below.
  • Cooling after hot rolling is executed while injecting a gas mixture of oxygen and an inert gas whose oxygen fraction is less than 20 vol% or an inert gas.
  • the oxygen fraction is preferably 10 vol% or less, more preferably 5 vol% or less, and further more preferably 0 vol% (that is, the inert gas only).
  • Argon, nitrogen and the like can be cited as the inert gas, and nitrogen is preferable.
  • the cooling stopping temperature in cooling executed while injecting the gas described above is not particularly limited, cooling may be executed to approximately 550-650°C for example while injecting the gas described above, and cooling may be executed thereafter to the room temperature in the atmospheric air.
  • the C amount is an element greatly affecting the mechanical properties of steel.
  • the C amount was stipulated to be 0.05% or more.
  • the C amount is preferably 0.15% or more, more preferably 0.3% or more.
  • the C amount was stipulated to be 1.2% or less.
  • the C amount is preferably 1.1% or less, more preferably 1.0% or less.
  • Si is an element required for deoxidizing steel. When its content is too low, formation of Fe 2 SiO 4 (fayalite) becomes insufficient, and the MD performance deteriorates. Therefore, the Si amount was stipulated to be 0.01% or more. The Si amount is preferably 0.1% or more, more preferably 0.2% or more. On the other hand, when the Si amount is excessively high, by excessive formation of Fe 2 SiO 4 (fayalite), such problems occur that the MD performance extremely deteriorates, a surface decarburized layer is formed, and the like. Therefore, the Si amount was stipulated to be 0.5% or less. The Si amount is preferably 0.45% or less, more preferably 0.4% or less.
  • Mn is an element useful in securing the quenchability of steel and increasing the strength. In order to effectively exert such actions, the Mn amount was stipulated to be 0.1% or more. The Mn amount is preferably 0.2% or more, more preferably 0.4% or more. On the other hand, when the Mn amount is excessively high, segregation occurs in the cooling step after the hot rolling, and super-cooled structure (martensite and the like) harmful for the drawability and the like is liable to be generated. Therefore, the Mn amount was stipulated to be 1.5% or less. The Mn amount is preferably 1.4% or less, more preferably 1.2% or less.
  • the P amount is an element deteriorating the toughness and ductility of steel.
  • the P amount was stipulated to be 0.02% or less.
  • the P amount is preferably 0.01% or less, more preferably 0.005% or less.
  • the lower limit of the P amount is not particularly limited, it is approximately 0.001% normally.
  • S is an element deteriorating the toughness and ductility of steel.
  • the S amount was stipulated to be 0.02% or less.
  • the S amount is preferably 0.01% or less, more preferably 0.005% or less.
  • the lower limit of the S amount is not particularly limited, it is approximately 0.001% normally.
  • N 0.005% or less (not including 0%)
  • N is an element deteriorating the ductility of steel when the content thereof becomes excessively high. Therefore, the N amount was stipulated to be 0.005% or less.
  • the N amount is preferably 0.004% or less, more preferably 0.003% or less.
  • the lower limit of the N amount is not particularly limited, it is approximately 0.001% normally.
  • the fundamental composition of the steel wire material of the present invention is as described above, and the balance is substantially iron.
  • inclusion of unavoidable impurities brought in due to situations of raw materials, materials, manufacturing facilities and the like in the steel wire material is allowed as a matter of course.
  • Both of Cr and Ni are elements enhancing the quenchability of steel and contributing to increase the strength.
  • the Cr amount is preferably 0.05% or more and the Ni amount is preferably 0.03% or more. Both of the Cr amount and Ni amount are more preferably 0.10% or more, and further more preferably 0.12% or more.
  • both of the Cr amount and Ni amount are preferably 0.3% or less, more preferably 0.25% or less, and further more preferably 0.20% or less.
  • the Cu is an element having an action of promoting peeling of the scale.
  • the Cu amount is preferably 0.01% or more, more preferably 0.05% or more, and further more preferably 0.10% or more.
  • the Cu amount is preferably 0.2% or less, more preferably 0.17% or less, and further more preferably 0.15% or less.
  • All of Nb, V, Ti, Hf and Zr are elements forming fine carbonitride and contributing to increase the strength.
  • all of the Nb amount, V amount, Ti amount, Hf amount and Zr amount are preferably 0.003% or more, more preferably 0.007% or more, and further more preferably 0.01% or more.
  • the total amount thereof is preferably 0.1% or less, more preferably 0.08% or less, and further more preferably 0.06% or less.
  • Al 0.1% or less (not including 0%)
  • the Al amount is an element effective as a deoxidizing agent.
  • the Al amount is preferably 0.001% or more, more preferably 0.005% or more, and further more preferably 0.01% or more.
  • the Al amount is preferably 0.1% or less, more preferably 0.08% or less, and further more preferably 0.06% or less.
  • the B is an element suppressing formation of ferrite by being present as free B (B that does not form the compound) solid-solved in steel, and is an element effective particularly in a high strength wire material which requires suppression of a longitudinal crack.
  • the B amount is preferably 0.0001% or more, more preferably 0.0005% or more, and further more preferably 0.0010% or more.
  • the B amount is preferably 0.005% or less, more preferably 0.0040% or less, and further more preferably 0.0035% or less.
  • Both of Ca and Mg are elements having an action of controlling the form of the inclusions and enhancing the ductility. Further, Ca also has an action of enhancing the corrosion resistance of the steel material. In order to exert such actions effectively, both of the Ca amount and the Mg amount are preferably 0.001% or more, more preferably 0.002% or more, and further more preferably 0.003% or more. On the other hand, when these elements are excessively high, the workability deteriorates. Therefore, both of the Ca amount and the Mg amount are preferably 0.01% or less, more preferably 0.008% or less, and further more preferably 0.005% or less.
  • the obtained steel wire material was measured by a method described below.
  • Samples with 10 mm length were taken from the front end, center part and rear end of the coil respectively, and the cross sections of the scale of optional three locations from each sample were observed using a scanning electron microscope (SEM) (observation magnification: 5,000 times).
  • SEM scanning electron microscope
  • the scale thickness was measured for 10 points at every 100 ⁇ m length in the peripheral direction of the steel wire material on each measurement location, the average scale thickness thereof was obtained, and the average value of the three locations was made the scale thickness of each sample. Further, the average value of respective samples (the front end, center part and rear end of the coil) was calculated, and was made the scale thickness of each test No.
  • samples with 10 mm length were taken from the front end, center part and rear end of the coil respectively, X-ray diffraction was performed for the cross sections of the scale of optional three locations from each sample, and the ratios (vol%) of FeO and Fe 2 SiO 4 were obtained from the peak intensity ratio of FeO, Fe 2 SiO 4 , Fe 2 O 3 and Fe 3 O 4 .
  • the average values of the three locations were made the FeO ratio and the Fe 2 SiO 4 ratio of each sample.
  • the average value of respective samples (the front end, center part and rear end of the coil) was calculated, and was made the FeO ratio and the Fe 2 SiO 4 ratio of each test No.
  • Samples with 200 mm length were taken from the front end, center part and rear end of the coil respectively, air was blown to the sample, and the scale on the surface of the steel wire material was blown out.
  • the appearance before and after blowing the air was photographed by a digital camera, and the area ratio of the scale having peeled off was obtained by comparing the both by image analysis.
  • Samples with 250 mm length were taken from the front end, center part and rear end of the coil respectively, were applied with deformation strain of 6% by a tensile test machine, and were taken out from the chuck. Air was thereafter blown to the sample, and the scale on the surface of the steel wire material was blown out. The appearance before and after application of the strain was photographed by a digital camera, and the area ratio of the remaining scale was calculated by comparing the both by image analysis.
  • Nos. 3, 29, 33, 36, 40, 43, 46, 47, 49 the MD property deteriorated, because the manufacturing condition did not satisfy the requirements of the present invention.
  • Nos. 3, 29, 36, 40, 43, 46, 47 are examples cooling was executed by injecting the atmospheric air after hot rolling, the FeO fraction could not be secured because FeO was converted to Fe 3 O 4 during cooling, and the MD property deteriorated.
  • No. 33 is an example the winding temperature after hot rolling was high, the scale thickness became thick, the FeO ratio increased excessively, the Fe 2 SiO 4 ratio was also high, and therefore the MD property deteriorated.
  • No. 49 is an example the winding temperature after hot rolling was low, the FeO ratio could not be secured, and the MD property deteriorated.
  • Nos. 50-54 are examples the winding temperature after hot rolling was further high, the scale thickness exceeded 7.0 ⁇ m, the scale peeling ratio of the rolled material increased, and the rust was generated. More specifically, in Nos. 50-54, it is considered that the scale drops during cooling after hot rolling and at the time of storage and transportation, and the rust is generated.
  • Fig. 2 the relation between the scale thickness and the scale peeling ratio of the rolled material is shown in Fig. 2 . It is known that the scale peeling ratio of the rolled material increases when the scale thickness becomes thick exceeding 7.0 ⁇ m.
  • the steel wire material of the present invention is excellent in the mechanical descaling performance after hot rolling (before drawing work), and is therefore useful as a raw material for a tire cord (steel cord, bead wire) for an automobile, hose wire, a saw wire and the like used for cutting a silicon for a semiconductor and the like.

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  • Organic Chemistry (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
EP12732406.9A 2011-01-07 2012-01-06 Stahldrahtmaterial und herstellungsverfahren dafür Withdrawn EP2662468A4 (de)

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JP2011002014A JP4980471B1 (ja) 2011-01-07 2011-01-07 鋼線材及びその製造方法
PCT/JP2012/050155 WO2012093715A1 (ja) 2011-01-07 2012-01-06 鋼線材及びその製造方法

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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
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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
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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
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WO2012093715A1 (ja) 2012-07-12
CN103314125B (zh) 2015-05-27
CN103314125A (zh) 2013-09-18
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

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