US20130272914A1 - Steel wire material and method for manufacturing same - Google Patents
Steel wire material and method for manufacturing same Download PDFInfo
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- US20130272914A1 US20130272914A1 US13/995,739 US201213995739A US2013272914A1 US 20130272914 A1 US20130272914 A1 US 20130272914A1 US 201213995739 A US201213995739 A US 201213995739A US 2013272914 A1 US2013272914 A1 US 2013272914A1
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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
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- 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
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- 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
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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
- 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
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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
- 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
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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
- 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
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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
- 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
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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
- 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
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- 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
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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
- 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
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- 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
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- 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.
- FIG. 1 is a graph showing the relation between the FeO ratio inside the scale and the remaining scale area ratio after MD.
- FIG. 2 is a graph showing the relation between the scale thickness and the scale peeling ratio of the rolled material.
- 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.
- 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 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.
- 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, 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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Abstract
The steel wire material of the present invention contains 0.05 to 1.2% of C (mass %; same for the chemical components hereafter), 0.01 to 0.5% of Si, 0.1 to 1.5% of Mn, 0.02% or less (but not 0%) of P, 0.02% or less (but not 0%) of S, and 0.005% or less (but not 0%) of N, with the balance being iron and inevitable impurities. The wire material has a scale layer that is no thicker than 7.0 μm or less. The scale layer has an FeO percentage of 30 to 80 vol % and an Fe2SiO4 percentage of less than 0.1 vol %. The scale layer that is formed will not peel when cooled after hot rolling or during storage and transport, but will easily peel during mechanical descaling.
Description
- 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.
- 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. As such 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.
- As methods for manufacturing a wire material formed with a scale with excellent MD performance, Patent Literatures 1-5 can be cited for example. In
Patent Literatures 1, 2, the scale amount remaining in the wire material after MD is reduced by forming a scale which is high in FeO ratio and thick. In 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. InPatent Literatures 4, 5, by controlling the area ratio of the holes inside the scale, the peeling performance of the scale is improved. - However, 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. - Also, it is difficult to stably lower the boundary face roughness by the method of lowering the boundary face roughness such as Patent Literature 3, it is difficult to stably form the holes even by the method of forming holes inside the scale such as
Patent Literatures 4, 5, and it is difficult to stably reduce the remaining scale amount according to either of these technologies. - Further, in these Patent Literatures 1-5, peeling off of the scale due to the compression stress generated during cooling is not considered at all, and there was a problem that the rust was generated in the wire material before MD by peeling off of the scale during cooling and at the time of storage and transportation.
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- [Patent Literature 1] Japanese Unexamined Patent Application Publication No. H4-293721
- [Patent Literature 2] Japanese Unexamined Patent Application Publication No. H11-172332
- [Patent Literature 3] Japanese Unexamined Patent Application Publication No. H8-295992
- [Patent Literature 4] Japanese Unexamined Patent Application Publication No. H10-324923
- [Patent Literature 5] Japanese Unexamined Patent Application Publication No. 2006-28619
- 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 μm or less thickness is included, FeO ratio inside the scale is 30-80 vol %, and Fe2SiO4 ratio is less than 0.1 vol %.
- According to the necessity, 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%).
- Further, 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.
- In the steel wire material of the present invention, the FeO ratio is appropriately controlled to a predetermined range (30-80 vol %), and a thin (7 μm 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.
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FIG. 1 is a graph showing the relation between the FeO ratio inside the scale and the remaining scale area ratio after MD. -
FIG. 2 is a graph showing the relation between the scale thickness and the scale peeling ratio of the rolled material. - In a cooling step during a manufacturing process of a wire material, normally, 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. As a result, 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. Also, 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. Conventionally, 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 Fe2O3 and Fe3O4. In order to increase the FeO ratio inside the scale, it is normally required to form a scale (a secondary scale formed in or after descaling before finish rolling) at a high temperature, however there was a problem that, when the scale was formed at a high temperature, the thickness of the scale increased, the scale loss increased, and the thick scale peeled off during the cooling step and at the time of storage and transportation. In other words, it was extremely difficult to make the thickness of the scale thin and to secure the FeO ratio inside the scale.
- So, as a result of studies by the present inventors, it was found out that, when the winding temperature after the hot rolling was made comparatively low temperature and cooling was thereafter executed while injecting a gas mixture of oxygen and an inert gas whose oxygen fraction was comparatively low or an inert gas, the scale could be made thin and the FeO ratio inside the scale could be secured by a predetermined ratio or more.
- When the thickness of the scale was studied in more detail, it was found out that, if the thickness of the scale was 7.0 μm or less, adhesiveness against the base iron was excellent, and the scale did not peel off in the middle of cooling and at the time of storage and transportation. The scale thickness is preferably 6.5 μm or less, more preferably 6.0 μm or less (particularly 5.5 μm or less). Although the lower limit of the scale thickness is not particularly limited, it is approximately 0.9 μm normally.
- Further, 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 N2-10 vol % O2 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. - According to
FIG. 1 , it is known that, when the FeO ratio inside the scale is 30-80 vol %, the remaining scale amount after MD can be reduced sufficiently. 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. - Also, the Fe2SiO4 (fayalite) ratio inside the scale is to be less than 0.1 vol %. When excessively formed, Fe2SiO4 is formed unevenly on the boundary face between the scale and the base iron, the scale unevenly peels off at the time of MD, and therefore the MD performance deteriorates. The Fe2SiO4 ratio is preferably 0.09 vol % or less, more preferably 0.08 vol % or less, and further more preferably 0.07 vol % or less. On the other hand, since Fe2SiO4 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 Fe2SiO4 by 0.01 vol % or more, more preferably 0.02 vol % or more, and further more preferably 0.03 vol % or more.
- In the scale in the present invention, Fe2O3, Fe3O4 and the like are included other than FeO and Fe2SiO4.
- By making the thickness of the scale and the area ratio of the fine holes as described above, 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.
- In order to form the scale described above, it is important to hot-roll the steel with the chemical composition described below, to thereafter execute winding at a comparatively low temperature (750-880° C.), and then to execute cooling while injecting a gas mixture of oxygen and an inert gas whose oxygen fraction is low or an inert gas. By executing winding at a low temperature, the scale can be made thin. Also, by injecting the gas whose oxygen fraction is low or not including oxygen as described above and executing cooling, FeO can be secured by a predetermined amount or more without converting FeO formed to Fe3O4.
- When the winding temperature after hot rolling exceeds 880° C., the scale thickness exceeds 7.0 μm, the FeO ratio inside the scale exceeds 80 vol %, and the MD performance deteriorates. Also, when the winding temperature exceeds 880° C., Fe2SiO4 (fayalite) 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. On the other hand, when 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. By cooling while injecting such a gas with low oxygen fraction or not containing oxygen, FeO already formed can be prevented from being converted to Fe3O4, and the FeO ratio inside the scale can be secured. 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. Although 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.
- Below, the chemical composition of the steel wire material of the present invention will be described.
- C is an element greatly affecting the mechanical properties of steel. In order to secure the strength of the wire material, 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. On the other hand, when the C amount is excessively high, the hot workability in manufacturing the wire material deteriorates. Therefore, 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 Fe2SiO4 (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 Fe2SiO4 (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.
- P is an element deteriorating the toughness and ductility of steel. In order to prevent the wire breakage in the drawing step and the like, 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. Although the lower limit of the P amount is not particularly limited, it is approximately 0.001% normally.
- Similarly to P, S is an element deteriorating the toughness and ductility of steel. In order to prevent the wire breakage in the drawing step and the twisting step thereafter, 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. Although the lower limit of the S amount is not particularly limited, it is approximately 0.001% normally.
- 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. Although 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. However, 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. Further, it is also recommended to add elements described below according to the necessity within a range not impeding the actions and effects of the present invention.
- Cr: 0.3% or Less (not Including 0%) and/or Ni: 0.3% or Less (not Including 0%)
- Both of Cr and Ni are elements enhancing the quenchability of steel and contributing to increase the strength. In order to exert such actions effectively, 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. On the other hand, when the Cr amount and Ni amount are excessively high, the martensite structure is liable to be generated, adhesiveness of the scale and the base iron increases excessively high, and the peeling performance of the scale at the time of MD deteriorates. Therefore, 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.
- Cu is an element having an action of promoting peeling of the scale. In order to exert such action effectively, the Cu amount is preferably 0.01% or more, more preferably 0.05% or more, and further more preferably 0.10% or more. On the other hand, when the Cu amount is excessively high, peeling of the scale is promoted excessively, the scale peels off during rolling, other scales which are thin and highly adhesive are generated on the peeled surface, and the rust is generated when the wire material coil is stored and transported. Therefore, the Cu amount is preferably 0.2% or less, more preferably 0.17% or less, and further more preferably 0.15% or less.
- At Least One Element Selected from a Group Consisting of Nb, V, Ti, Hf and Zr: 0.1% Or Less (not Including 0%) in Total
- All of Nb, V, Ti, Hf and Zr are elements forming fine carbonitride and contributing to increase the strength. In order to exert such actions effectively, 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. On the other hand, when these elements are excessively high, the ductility deteriorates, and therefore 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 is an element effective as a deoxidizing agent. In order to exert such action effectively, the Al amount is preferably 0.001% or more, more preferably 0.005% or more, and further more preferably 0.01% or more. On the other hand, when the Al amount is excessively high, oxide-based inclusions such as Al2O3 and the like increase, and wire breakage frequently occurs in drawing work and the like. Therefore, the Al amount is preferably 0.1% or less, more preferably 0.08% or less, and further more preferably 0.06% or less.
- 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. In order to exert such actions effectively, the B amount is preferably 0.0001% or more, more preferably 0.0005% or more, and further more preferably 0.0010% or more. On the other hand, when the B amount is excessively high, the ductility deteriorates. Therefore, the B amount is preferably 0.005% or less, more preferably 0.0040% or less, and further more preferably 0.0035% or less.
- Ca: 0.01% or Less (not Including 0%) and/or Mg: 0.01% or Less (not Including 0%)
- 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.
- Below, the present invention will be explained more specifically referring to an example. The present invention is not limited by the example described below, and it is a matter of course that the present invention can also be implemented with modifications being added appropriately within the scope adaptable to the purposes described above and below, and any of them is to be included within the technical range of the present invention.
- After steel of the chemical composition shown in Tables 1, 2 was smelted according to an ordinary smelting method, a billet of 150 mm×150 mm was manufactured and was heated inside a heating furnace. Thereafter, the primary scale formed inside the heating furnace was descaled using high-pressure water, hot rolling was executed under the conditions (the winding temperature after hot rolling and the gas used for cooling) shown in Table 3, and the steel wire material of Φ5.5 mm was obtained. Also, cooling using the gas shown in Table 3 was executed to approximately 600° C. in all cases, and the wire material was left for cooling in the atmospheric air.
- 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). The scale thickness was measured for 10 points at every 100 μm 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.
- Similarly to above (1), 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 Fe2SiO4 were obtained from the peak intensity ratio of FeO, Fe2SiO4, Fe2O3 and Fe3O4. The average values of the three locations were made the FeO ratio and the Fe2SiO4 ratio 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 FeO ratio and the Fe2SiO4 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.
- The results are shown in Tables 4, 5 and
FIG. 2 . -
TABLE 1 Chemical composition (mass %) with the remainder being iron and unavoidable impurities Steel kind C Si Mn P S N Cr Ni Cu Al B Others A-1 0.80 0.25 0.55 0.007 0.003 0.002 — — — — — — A-2 0.80 0.25 0.55 0.007 0.003 0.002 0.28 — — — — — A-3 0.80 0.25 0.55 0.007 0.003 0.002 — 0.23 — A-4 0.80 0.25 0.55 0.007 0.003 0.002 — — 0.18 — — — A-5 0.80 0.25 0.55 0.007 0.003 0.002 — — — 0.025 — — A-6 0.80 0.25 0.55 0.007 0.003 0.002 — — — 0.0005 — A-7 0.80 0.25 0.55 0.007 0.003 0.002 — — — — — V = 0.035 A-8 0.80 0.25 0.55 0.007 0.003 0.002 — — — — — Ca = 0.004 A-9 0.80 0.25 0.55 0.007 0.003 0.002 — — — — — Hf = 0.052 A-10 0.80 0.25 0.55 0.007 0.003 0.002 — — — — — Ti = 0.038 A-11 0.80 0.25 0.55 0.007 0.003 0.002 — — — — — Mg = 0.003 A-12 0.80 0.25 0.55 0.007 0.003 0.002 — — — — — Nb = 0.031 A-13 0.80 0.25 0.55 0.007 0.003 0.002 — — — — — Zr = 0.056 A-14 0.80 0.25 0.55 0.007 0.003 0.002 0.23 0.03 — — — — A-15 0.80 0.25 0.55 0.007 0.003 0.002 0.14 0.13 0.07 — — — A-16 0.80 0.25 0.55 0.007 0.003 0.002 0.05 0.09 — 0.011 — — A-17 0.80 0.25 0.55 0.007 0.003 0.002 0.12 0.25 — — 0.0011 — A-18 0.80 0.25 0.55 0.007 0.003 0.002 0.08 0.08 — — — Ti = 0.072 A-19 0.80 0.25 0.55 0.007 0.003 0.002 0.05 — 0.05 — — — A-20 0.80 0.25 0.55 0.007 0.003 0.002 0.16 — 0.14 0.028 — — A-21 0.80 0.25 0.55 0.007 0.003 0.002 — 0.15 0.09 — — — A-22 0.80 0.25 0.55 0.007 0.003 0.002 — 0.28 0.17 0.035 — — A-23 0.80 0.25 0.55 0.007 0.003 0.002 — 0.12 0.06 — 0.0009 — A-24 0.80 0.25 0.55 0.007 0.003 0.002 — 0.07 0.15 — — Hf = 0.054 -
TABLE 2 Chemical composition (mass %) with the remainder being iron and unavoidable impurities Steel kind C Si Mn P S N Cr Ni Cu Al B Others B 0.06 0.08 0.12 0.003 0.005 0.002 0.12 0.03 — 0.01 — V = 0.029 C 0.19 0.17 0.42 0.003 0.001 0.002 — — 0.04 0.021 — — D 0.44 0.38 0.88 0.002 0.003 0.002 — — — — — Ca = 0.002 E 0.69 0.45 0.76 0.002 0.004 0.002 — 0.01 0.02 — 0.0005 Ti = 0.031, Hf = 0.027 F 0.88 0.37 0.46 0.002 0.003 0.002 0.27 — 0.03 0.015 — — G 0.92 0.48 0.98 0.002 0.003 0.002 0.18 0.23 0.02 — — Ca = 0.003 H 1.05 0.29 1.15 0.004 0.003 0.002 0.26 0.02 0.16 0.002 0.0021 Ti = 0.026, Hf = 0.022 I 1.19 0.32 1.32 0.002 0.001 0.002 0.03 0.14 0.12 0.001 0.0034 Zr = 0.027, Nb = 0.043 -
TABLE 3 Manufac- Winding turing temperature condition (° C.) Cooling gas composition a 750 Nitrogen b 760 Atmospheric air c 800 Nitrogen + 1 vol % oxygen d 850 Nitrogen + 5 vol % oxygen e 875 Nitrogen + 10 vol % oxygen f 880 Atmospheric air g 890 Nitrogen h 740 Nitrogen i 970 Atmospheric air -
TABLE 4 MD performance Scale peeling Remaining scale Scale ratio of rolled area ratio after Steel Manufacturing thickness FeO ratio Fe2SiO4 ratio material applying 6% strain No. kind condition (μm) (vol %) (vol %) (area %) (%) 1 A-1 a 1.5 35 0.02 0.6 28 2 A-1 d 4.6 47 0.05 0.8 18 3 A-1 b 1.2 26 0.01 1.9 35 4 A-2 a 1.9 36 0.03 0.8 21 5 A-3 c 2.3 39 0.01 0.6 18 6 A-4 d 5.9 63 0.05 0.5 10 7 A-5 e 6.8 67 0.06 0.2 8 8 A-6 c 3.2 52 0.01 0.6 13 9 A-7 a 1.3 41 0.02 0.5 17 10 A-8 d 4.4 52 0.01 0.8 16 11 A-9 e 6.1 72 0.08 0.6 19 12 A-10 a 2.4 33 0.02 0.9 20 13 A-11 e 7.0 79 0.03 0.8 29 14 A-12 d 6.5 53 0.07 1.1 11 15 A-13 c 2.4 36 0.01 0.8 16 16 A-14 a 1.9 34 0.01 1.2 24 17 A-15 c 2.7 39 0.02 0.9 25 18 A-16 d 4.5 48 0.02 0.7 12 19 A-17 e 5.3 56 0.05 0.5 5 20 A-18 c 3.4 43 0.03 0.6 11 21 A-19 e 5.5 61 0.09 0.7 9 22 A-20 d 4.1 46 0.04 0.8 12 23 A-21 a 1.3 31 0.03 0.9 18 24 A-22 c 1.9 42 0.02 0.4 14 25 A-23 d 3.8 47 0.02 0.5 12 26 A-24 e 5.4 55 0.05 1.1 7 -
TABLE 5 MD performance Scale peeling Remaining scale Scale ratio of rolled area ratio after Steel Manufacturing thickness FeO ratio Fe2SiO4 ratio material applying 6% strain No. kind condition (μm) (vol %) (vol %) (area %) (%) 27 B a 1.1 39 0.02 0.8 16 28 B c 1.8 44 0.03 1 13 29 B b 1.5 21 0.02 1.8 41 30 C c 2.4 42 0.04 0.8 15 31 C d 3.6 58 0.04 0.5 11 32 D e 5.5 71 0.05 0.7 22 33 D g 8.8 82 0.16 0.03 32 34 E c 2.5 32 0.03 0.9 27 35 E e 5.6 44 0.04 0.7 19 36 E f 6.1 25 0.04 1.9 31 37 F d 3.4 45 0.02 0.9 17 38 F a 1.5 31 0.01 0.8 24 39 F e 4.1 54 0.02 0.6 10 40 F b 1.6 14 0.01 1.9 52 41 G a 1.5 44 0.01 1 14 42 G d 3.2 57 0.04 0.5 7 43 G f 6.0 27 0.05 1.8 35 44 H a 0.9 31 0.01 0.7 18 45 H e 4.5 61 0.03 0.6 10 46 H b 1.8 8 0.02 1.8 56 47 H f 6.7 19 0.08 1.9 43 48 I d 4.8 68 0.05 0.8 14 49 I h 0.8 6 0.01 1.8 59 50 A-1 i 7.1 41 0.02 2.9 10 51 B i 7.5 38 0.01 3.5 11 52 E i 8.2 45 0.03 5.7 9 53 G i 7.8 42 0.02 4.2 12 54 I i 8.5 35 0.01 6.1 4 - Nos. 1, 2, 4-28, 30-32, 34, 35, 37-39, 41, 42, 44, 45, 48 of Tables 4, 5 are examples satisfying the requirements of the present invention, the scale thickness and the composition of the scale are appropriate, and therefore the MD property is excellent.
- On the other hand, in 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 Fe3O4 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 Fe2SiO4 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 μm, 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.
- Also, 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 μm. - The present invention has been described in detail and referring to a specific embodiment, however, it is clear for a person with an ordinary skill in the art that a variety of alterations and modifications can be added without departing from the spirit and scope of the present invention.
- The present application is based on the Japanese Patent Application No. 2011-002014 applied on Jan. 7, 2011, and the contents thereof are hereby incorporated by reference.
- 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.
Claims (4)
1. A steel wire material comprising, by mass % based on the total mass of the steel wire material:
C: 0.05-1.2%;
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, wherein
a scale with 7.0 μm or less thickness is included,
FeO ratio inside the scale is 30-80 vol %, and
Fe2SiO4 ratio is less than 0.1 vol %.
2. The steel wire material according to claim 1 , further comprising, by mass % based on the total mass of the steel wire material, at least one selected from the group of (1) (2), (3), (4), (5), and (6):
(1) Cr: 0.3% or less (not including 0%) and/or Ni: 0.3% or less (not including 0%);
(2) Cu: 0.2% or less (not including 0%);
(3) 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;
(4) Al: 0.1% or less (not including 0%);
(5) B: 0.005% or less (not including 0%); and
(6) Ca: 0.01% or less (not including 0%) and/or Mg: 0.01% or less (not including 0%).
3. A method for manufacturing a steel wire material, the method comprising:
hot rolling steel of the chemical composition according to claim 1 , to obtain a hot rolled steel;
thereafter winding up the hot rolled steel at 750-880° C., to obtain a wound steel; and
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.
4. The method for manufacturing according to claim 3 , wherein the inert gas is nitrogen.
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
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JP2011002014A JP4980471B1 (en) | 2011-01-07 | 2011-01-07 | Steel wire rod and manufacturing method thereof |
JP2011-002014 | 2011-01-07 | ||
PCT/JP2012/050155 WO2012093715A1 (en) | 2011-01-07 | 2012-01-06 | Steel wire material and method for producing same |
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US20130272914A1 true US20130272914A1 (en) | 2013-10-17 |
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US13/995,739 Abandoned US20130272914A1 (en) | 2011-01-07 | 2012-01-06 | Steel wire material and method for manufacturing same |
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US (1) | US20130272914A1 (en) |
EP (1) | EP2662468A4 (en) |
JP (1) | JP4980471B1 (en) |
KR (2) | KR20140076642A (en) |
CN (1) | CN103314125B (en) |
WO (1) | WO2012093715A1 (en) |
Cited By (2)
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CN113330124A (en) * | 2018-12-31 | 2021-08-31 | 贝克休斯能源科技英国有限公司 | Steel wire |
US11220136B2 (en) | 2017-04-28 | 2022-01-11 | Bridgestone Corporation | Steel cord for reinforcing rubber article, method for manufacturing same, and tire |
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CN105088063B (en) * | 2014-05-19 | 2017-04-26 | 上海梅山钢铁股份有限公司 | Work-hardening high-strength steel and manufacturing method thereof |
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BR112017020004A2 (en) * | 2015-04-08 | 2018-06-19 | Nippon Steel & Sumitomo Metal Corporation | steel sheet for heat treatment |
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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 (en) * | 2015-12-07 | 2016-11-15 | 주식회사 포스코 | High carbon steel wire rod and steel wire having excellent hydrogen induced cracking resistance and method for manufacturing thereof |
JP6757194B2 (en) * | 2016-07-11 | 2020-09-16 | 日本パーカライジング株式会社 | Pre-heat treatment carbon steel with excellent scale removal properties, post-heat treatment carbon steel and their manufacturing methods, scale removal methods and easily descalable film forming agents |
EP3613898A4 (en) * | 2017-04-17 | 2021-02-17 | Bridgestone Corporation | Cable bead and airplane tire using same |
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 |
CN110560495A (en) * | 2019-09-17 | 2019-12-13 | 安徽工业大学 | Laboratory scale removal experiment platform and experiment method thereof |
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JP2969293B2 (en) | 1991-03-22 | 1999-11-02 | 新日本製鐵株式会社 | Manufacturing method of mild steel wire rod with excellent mechanical descaling |
JP3265123B2 (en) * | 1994-06-03 | 2002-03-11 | 新日本製鐵株式会社 | Wire material with excellent mechanical descaling and drawing properties |
JP3434080B2 (en) | 1995-04-21 | 2003-08-04 | 新日本製鐵株式会社 | Wire for descaling |
JPH10324923A (en) | 1997-05-27 | 1998-12-08 | Nippon Steel Corp | Wire rod for steel wire |
JPH11172332A (en) | 1997-12-15 | 1999-06-29 | Sumitomo Metal Ind Ltd | High carbon steel wire rod |
JP2000246322A (en) * | 1999-02-25 | 2000-09-12 | Kobe Steel Ltd | Rolled wire rod superior in acid pickling property, and its manufacturing method |
JP4159706B2 (en) * | 1999-07-19 | 2008-10-01 | 株式会社神戸製鋼所 | Steel wire rod with excellent scale peelability during mechanical descaling |
JP3744279B2 (en) * | 1999-09-09 | 2006-02-08 | Jfeスチール株式会社 | Method for producing high carbon hot-rolled steel sheet with excellent scale adhesion |
JP2005281793A (en) * | 2004-03-30 | 2005-10-13 | Sumitomo Metal Ind Ltd | Method for producing wire rod for steel wire, and wire rod for steel wire |
JP4375149B2 (en) | 2004-07-21 | 2009-12-02 | 住友金属工業株式会社 | High strength low alloy steel wire |
JP4971719B2 (en) * | 2005-08-12 | 2012-07-11 | 株式会社神戸製鋼所 | Steel wire rod for mechanical descaling |
EP1921172B1 (en) * | 2005-08-12 | 2012-11-28 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Method for production of steel material having excellent scale detachment property, and steel wire material having excellent scale detachment property |
JP4704978B2 (en) * | 2006-08-28 | 2011-06-22 | 株式会社神戸製鋼所 | A method for producing steel with excellent scale peelability. |
JP5084206B2 (en) * | 2006-09-12 | 2012-11-28 | 株式会社神戸製鋼所 | Manufacturing method of steel wire with excellent drawability |
-
2011
- 2011-01-07 JP JP2011002014A patent/JP4980471B1/en not_active Expired - Fee Related
-
2012
- 2012-01-06 EP EP12732406.9A patent/EP2662468A4/en not_active Withdrawn
- 2012-01-06 KR KR1020147014715A patent/KR20140076642A/en not_active Application Discontinuation
- 2012-01-06 KR KR1020137017580A patent/KR20130087613A/en active Application Filing
- 2012-01-06 WO PCT/JP2012/050155 patent/WO2012093715A1/en active Application Filing
- 2012-01-06 US US13/995,739 patent/US20130272914A1/en not_active Abandoned
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Cited By (2)
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US11220136B2 (en) | 2017-04-28 | 2022-01-11 | Bridgestone Corporation | Steel cord for reinforcing rubber article, method for manufacturing same, and tire |
CN113330124A (en) * | 2018-12-31 | 2021-08-31 | 贝克休斯能源科技英国有限公司 | Steel wire |
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WO2012093715A1 (en) | 2012-07-12 |
CN103314125B (en) | 2015-05-27 |
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EP2662468A1 (en) | 2013-11-13 |
KR20140076642A (en) | 2014-06-20 |
JP4980471B1 (en) | 2012-07-18 |
JP2012144756A (en) | 2012-08-02 |
EP2662468A4 (en) | 2015-05-27 |
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