EP3115478B1 - High-carbon steel wire having superior wire drawing properties and method for producing same - Google Patents

High-carbon steel wire having superior wire drawing properties and method for producing same Download PDF

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Publication number
EP3115478B1
EP3115478B1 EP15759266.8A EP15759266A EP3115478B1 EP 3115478 B1 EP3115478 B1 EP 3115478B1 EP 15759266 A EP15759266 A EP 15759266A EP 3115478 B1 EP3115478 B1 EP 3115478B1
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Prior art keywords
wire rod
less
wire
bainite
transformation
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German (de)
English (en)
French (fr)
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EP3115478A1 (en
EP3115478A4 (en
Inventor
Toshiyuki Manabe
Tatsusei Tada
Daisuke Hirakami
Arata Iso
Susumu Sahara
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/64—Patenting furnaces
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite

Definitions

  • the present invention relates to a high carbon steel wire rod requiring primary wire drawing before final patenting or oil tempering or a high carbon steel wire rod for use in the manufacture of an ACSR (aluminum conductor steel reinforced) and rope, and relates to a method for production of the same.
  • the drawing process For secondary working of a wire rod, mainly the drawing process is used.
  • pearlite steel heat-treated by the Stelmor process or lead patenting process is used.
  • ultrafine wire of STC (steel cord) or small diameter rope is produced by the steps of reducing the wire rod in size to a predetermined wire diameter by intermediate patenting or reducing the rolled wire size so as to decrease the strain in wire drawing.
  • the present invention was made taking note of the above situation and has as its object the provision of a wire rod having stable and good wire drawing characteristics in actual production and a method for production of that wire rod.
  • the inventions disclosed in PLTs 1 to 3 all hold the temperatures of the rods at 350°C to 500°C for within a certain time so as start partial bainite transformation from the supercooled austenite structure, then cause the temperature to rise and hold the temperatures of the rods there until the bainite transformation completely ends to thereby produce a bainite structure with precipitation of coarse cementite. That is, the inventions disclosed in PLTs 1 to 3 are all characterized by softening the upper bainite structure during two-stage heat treatment. They are not directed to completion of the bainite transformation by single-stage heat treatment.
  • the present invention was made based on the above discoveries and has as its gist the following:
  • FIG. 1 is a view showing one example of the relationship between the tensile strength TS (MPa) and amount of C (mass%).
  • the wire rod excellent in wire drawing ability of the present invention (below, sometimes referred to as “the wire rod of the present invention") is characterized by having a chemical composition comprising, by mass%, C: 0.7 to 1.2%, Si: 0.1 to 1.5%, Mn: 1.0% or less and a balance of Fe and unavoidable impurities, in which 80% or more of a microstructure is a bainite structure and a remaining microstructure is a nonbainite structure in the cross-section of the wire rod, a full width at half maximum of a (211) crystal face of a ferrite phase in the structure of the wire rod cross-section is 0.6° or less, further a tensile strength TS (MPa) and reduction of area RA (%) respectively satisfy the following formula (1) and the following formula (2), and a standard deviation of hardness distribution of Vickers hardness (Hv) in the cross-section is less than 6.
  • a chemical composition comprising, by mass%, C: 0.7 to 1.2%, Si: 0.1 to 1.5%,
  • the "wire rod cross-section” means the cross-section vertical to the length direction of the wire rod.
  • C is an element increasing the cementite fraction and number density of cementite in the bainite structure and the dislocation density to raise the strength. If less than 0.7%, due to the ferrite transformation at the time of heat treatment, securing the bainite fraction becomes difficult, therefore the content is made 0.7% or more. Preferably, the content is 0.9% or more. On the other hand, if over 1.2%, proeutectoid cementite precipitates and the wire drawing ability deteriorates, so the content is made 1.2% or less. Preferably, the content is made 1.0% or less.
  • Si is a deoxidizing element. Further, it is an element of solid solution strengthening the ferrite. If less than 0.1%, at the time of galvanization, the alloy layer is not stably formed, so the content is made 0.1% or more. Preferably, the content is made 0.4% or more. On the other hand, if over 1.5%, the decarburization at the time of heating is promoted, the mechanical descaling ability deteriorates, and the precipitation of carbides at the time of the bainite transformation is also delayed, so the content is made 1.5% or less. Preferably, the content is made 1.2% or less.
  • Mn is a deoxidizing element. Further, it is an element improving the hardenability. It suppresses the formation of ferrite at the time of heat treatment, but if over 1.0%, the transformation is slowed and non transformed structures may be formed, so the content is made 1.0% or less. Preferably, the content is made 0.7% or less.
  • the lower limit is not particularly set, but from the viewpoint of increasing the ratio of the bainite structure, 0.2% or more is preferable, while 0.3% or more is more preferable.
  • the wire rod of the present invention may contain, in addition to the above elements, one or more of Cr, Ni, Cu, V, Mo, Ti, Nb, Al, Ca, and B in suitable quantities in a range not impairing the characteristics of the wire rod of the present invention.
  • Cr is an element improving the hardenability and an element which acts to suppress the ferrite transformation and pearlite transformation at the time of heat treatment. If over 1.0%, the transformation finish time becomes longer and also the mechanical descaling ability deteriorates, so the content is made 1.0% or less. Preferably, it is 0.7% or less.
  • the lower limit includes 0%, but from the viewpoint of reliably obtaining the effect of addition, 0.05% or more is preferable.
  • Ni is an element improving the hardenability and an element suppressing ferrite transformation to increase the ratio of the bainite structure. If over 1.0%, the transformation finish time become longer, so the content is made 1.0% or less. Preferably, it is made 0.7% or less.
  • the lower limit includes 0%, but from the viewpoint of reliably obtaining the effect of addition, 0.05% or more is preferable.
  • Cu is an element improving the corrosion resistance. If over 0.1%, it reacts with S to cause CuS to segregate at the austenite grain boundaries, which causes scratches at the steel ingots or wire rods etc. in the process of production of wire rods, so the content is made 0.1% or less. Preferably, it is made 0.07% or less.
  • the lower limit includes 0%, but from the viewpoint of reliably obtaining the effect of addition, 0.01% or more is preferable.
  • V is an element acting to delay ferrite transformation in the solid solution state. If over 0.1%, it forms nitrides in the austenite structure and causes the hardenability to drop. Further, when raising the temperature after transformation, carbides precipitate and the wire falls in toughness. Therefore, the content is made 0.1% or less. Preferably, the content is made 0.05% or less, more preferably 0.03% or less. The lower limit includes 0%, but from the viewpoint of reliably obtaining the effect of addition, 0.01% or more is preferable.
  • Mo is an element improving the hardenability, suppressing ferrite transformation and pearlite transformation, and raising the ratio of the bainite structure. If over 0.5%, the transformation finish time becomes longer and also, when raising the temperature after transformation, carbides are formed and secondary hardening occurs, so the content is made 0.5% or less. Preferably, the content is made 0.3% or less.
  • the lower limit includes 0%, but from the viewpoint of reliably obtaining the effect of addition, 0.1% or more is preferable.
  • Ti is an element reducing the ⁇ -grain size and refining the subsequently formed structure and thereby contributes to improvement of the ductility. If over 0.05%, the effect of addition is saturated, so the content is made 0.05% or less. Preferably, the content is made 0.02% or less.
  • the lower limit includes 0%, but from the viewpoint of reliably obtaining the effect of addition, 0.005% or more is preferable.
  • Nb is an element improving the hardenability. Further, a nitride of Nb acts as pinning particles, so Nb is an element which contributes to control of the transformation time and grain size at the time of heat treatment. If over 0.1%, the transformation finish time becomes longer, so the content is made 0.1% or less. Preferably, the content is made 0.07% or less.
  • the lower limit includes 0%, but from the viewpoint of reliably obtaining the effect of addition, 0.005% or more is preferable.
  • Al is an element effective as a deoxidizing element. If over 0.1%, hard inclusions are formed and the wire drawing ability falls, so the content is made 0.1% or less. Preferably, the content is made 0.07% or less.
  • the lower limit includes 0%, but from the viewpoint of reliably obtaining the effect of addition, 0.02% or more is preferable.
  • Ca is a deoxidizing element. Further, it is an element effective for controlling the form of inclusions in the steel. If over 0.05%, coarse inclusions are formed, so the upper limit is made 0.05% or less. Preferably, the content is made 0.02% or less.
  • the lower limit includes 0%, but from the viewpoint of reliably obtaining the effect of addition, 0.001% or more is preferable.
  • the content is made 0.005% or less.
  • the content is made 0.002% or less.
  • the lower limit includes 0%, but from the viewpoint of reliably obtaining the effect of addition, 0.0003% or more is preferable.
  • N Nitrogen bonds with the nitride-forming elements such as Al and Ti to form precipitates in the steel material, which act as pinning particles at the austenite grain boundaries. Further, N present as a solid solution element causes the reduction of area to drop at the time of a tensile test. Further, if the amount of N exceeds 0.005%, the austenite grain boundaries become finer, the targeted bainite structure becomes difficult to obtain, and the reduction of area of the wire rod falls, so the upper limit is made 0.005%.
  • the microstructure of the wire rod of the present invention is characterized in that, in the wire rod cross-section, 80% or more in terms of area ratio is a bainite structure and the remainder is a nonbainite structure and in that a full width at half maximum of a (211) crystal face of a ferrite phase in the microstructure of the wire rod cross-section is 0.6° or less.
  • the inventors researched seriously the range in which a nonbainite structure will not affect the strength of the wire rod as a whole or the wire after wire drawing. As a result, they discovered that if the nonbainite structure is less than 20%, there is no effect on the strength of the wire rod as a whole or the wire after wire drawing. Based on this discovery, they defined the ratio of the bainite structure in the wire rod cross-section as 80% or more.
  • the ratio of the bainite structure can be determined by taking a sample of the wire rod whose cross-section perpendicular to the length direction is used as an observed surface, polishing the observed surface, subjecting it to Nital etching,or Le Pera etching according to need, and observing the observed surface using an optical microscope or electron microscope, or X-ray diffraction. By binarizing the microstructural photograph obtained by the optical microscope or electron microscope to white and black, it is possible to analyze the image and determine the area ratio of bainite.
  • the structural fraction may be determined by photographing a 1/4 part in the thickness direction of a sample obtained from an arbitrary position of the steel sheet by X1000 in a range of 300 ⁇ 300 ⁇ m, and measuring three or more such observed fields by the above method.
  • the bainite structure and nonbainite structure may also be distinguished by analyzing the measurement data on crystal orientations of the electron diffraction patterns obtained using EBSD (electron backscatter diffraction) by the KAM method (kernel average misorientation).
  • a bainite structure is comprised of carbides of granular cementite and a ferrite phase.
  • the ratio of the bainite structure of the wire rod of the present invention is substantially determined by the bainite transformation step comprised of heating and cooling after the later explained coiling step. Furthermore, by performing the later explained heat treatment step of heating the wire rod where the bainite transformation is finished, the inventors found that the full width at half maximum of the (211) crystal plane of the ferrite phase in the structure of the wire rod cross-section will fall and a wire rod having good wire drawing ability can be obtained in the case of the full width at half maximum being 0.6° or less.
  • full width at half maximum means a width of the angle at the position where the height is half of the peak height in the diffraction peak of a certain crystal plane measured by X-ray diffraction.
  • the pearlite structure contains a lot of elastic strain, so the full width at half maximum becomes high at the stage of formation of pearlite. Even if heating, it would be more difficult to decrease the full width at half maximum of the pearlite structure compared with the bainite structure. For this reason, the higher the pearlite fraction, the higher the full width at half maximum, so this is suitable as an indicator for evaluation of the formed structure.
  • the (211) crystal plane of the ferrite phase in the microstructure of the wire rod cross-section is closely related to the dispersed state of carbides of the granular cementite and the content of pearlite in the microstructure of the wire rod cross-section. Therefore, the full width at half maximum becomes a parameter for judging the magnitudes of the bainite fraction of the wire rod, the dispersed state of carbides of granular cementite in the bainite structure, and the content of pearlite. In actuality, the full width at half maximum tends to decrease along with an increase of the bainite fraction. Further, the full width at half maximum tends to decrease along with the uniformity of the dispersed state of cementite, to increase along with an increase of the content of pearlite being the nonbainite structure, and to decrease along with the drop in strength of the wire rod.
  • the wire rod of the present invention is characterized by having a tensile strength TS (MPa) and reduction of area RA (%) respectively satisfying the following formula (1) and the following formula (2): TS ⁇ 580 + 700 ⁇ C RA ⁇ 100 ⁇ 46 ⁇ C ⁇ 18 ⁇ Mn ⁇ 10 ⁇ Cr where, [C], [Mn], and [Cr] respectively indicate the mass% of C, Mn, and Cr.
  • the tensile strength TS and reduction of area RA of the bainite wire rod depend on the average distance between cementite particles, the dislocation density, and the block particle size. In particular, in the wire rod of the present invention, they depend on the amount of carbon corresponding to the cementite fraction.
  • the inventors investigated the relationship between the tensile strength TS and the amount of carbon ([C]) in the specific ranges of the ratio of the bainite structure and full width at half maximum of the ferrite phases. Further, the inventors investigated the relationship of the reduction of area RA and "100-46 ⁇ [C]-18 ⁇ [Mn]-10 ⁇ [Cr]".
  • FIG. 1 shows the results of investigation of the relationship between the tensile strength TS and the amount of carbon ([C]). It will be understood that the tensile strength satisfies the above formula (1). The inventors discovered that the reduction of area RA is good if satisfying the above formula (2).
  • the hardness distribution in the cross-section also influences the wire drawing characteristics.
  • the inventors discovered that by making the standard deviation of the distribution of hardness in the wire rod cross-section a Vickers hardness (Hv) of less than 6, a wire rod with good wire drawing characteristics is obtained.
  • the method for production of the wire rod of the present invention is characterized by hot rolling a billet of the chemical composition of the wire rod of the present invention into a wire rod, then winding it into a coil at 850 to 1050°C, next immersing it in 300 to 475°C molten salt or molten lead, completing the bainite transformation to obtain a bainite fraction of 80% or more, then immersing it in 550 to 650°C molten salt or molten lead for 15 seconds or more.
  • the wire rod temperature of the time of winding the wire rod up into a coil is important in the adjustment of austenite grain size.
  • the coiling temperature of a wire rod changes according to the hardenability of the type of steel. However, if over 1050°C, the terminal treatment of the wire rod becomes physically difficult, so the temperature is made 1050°C or less. Preferably, it is 1000°C or less.
  • the temperature is made 850°C or more.
  • it is 900°C or more.
  • another method for production of the wire rod of the present invention is characterized by heating a wire rod of a chemical composition of the present invention to 850°C or more, then immersing it in 300 to 475°C sand, molten salt, or molten lead for patenting to obtain 80% or more of a bainite structure in the cross-section of the wire rod, then using sand, molten salt, molten lead, or resistance heating or induction heating to heat it at 550 to 650°C for 1 second or more.
  • the heating temperature influences the hardenability of the steel material. If the heating temperature is less than 850°C, the austenite grain size becomes finer, the hardenability falls, the bainite fraction does not rise, and dual-phase decarburization of the surface layer part proceeds, so the temperature is made 850°C or more. Preferably, the temperature is 900°C or more.
  • the heating temperature is set in accordance with the amount of the alloy elements, so the upper limit of the heating temperature is not particularly set, but from the viewpoint of economy, 1150°C or less is preferable. More preferably, the temperature is 1100°C or less.
  • the temperature of the sand, molten salt, or molten lead where the wire rods obtained by hot rolling the billet or the wire rods after reheating the once cooled wire rods is immersed influences the bainite transformation temperature and cooling speed of the wire rods. If the cooling medium temperature exceeds 475°C, the cooling speed decreases and pearlite transformation occurs and conversion to bainite in the entire cross-section of the wire rod becomes difficult, so the temperature is made 475°C or less. Preferably, it is 450°C or less.
  • the temperature is 300°C or more.
  • the temperature is 350°C or more.
  • the present invention can reheat a once cooled wire rod to 850°C or more, then hold the wire rod at 300 to 475°C in temperature range to make the bainite transformation of the wire rod structure progress and make the bainite structure of the wire rod uniform.
  • the bainite structure is mainly produced at about 300°C to about 500°C in temperature, but the size of the bainite structure is affected by the temperature at the time of formation of the bainite structure.
  • the wire rod is held at 300 to 475°C in temperature range until 80% or more of the structure in the wire rod cross-section becomes a bainite structure, then is heated at 550 to 650°C for 1 second or more as explained below.
  • the holding time until the bainite transformation is completed or the holding time until the bainite fraction becomes 80% or more may be determined in advance by predetermined experiments. For example, it is possible to investigate in advance the correspondence relationships among the compositions of wire rods, the holding time for immersion in molten salt or molten lead or the holding time for patenting, and the temperature and bainite fraction at the time of the immersion in the molten salt or the molten lead or at the time of patenting and determine the above-mentioned holding time based on the results of the above-mentioned investigation. In this case, the extent of the bainite transformation has to be judged strictly corresponding to the actual measured values.
  • a heat treatment step is performed for heating the wire rod after the completion of the bainite transformation.
  • the heating temperature in this heat treatment step influences the recovery and softening of the bainite wire. If the heating temperature is less than 550°C, a sufficient softening effect is not obtained, so the heating temperature is made 550°C or more. Preferably, it is made 570°C or more. If over 650°C, Ostwald growth of the cementite progresses and the ductility of the wire rod decreases, so the temperature is made 650°C. Preferably, it is made 630°C or less.
  • the heating time after completion of the bainite transformation is adjusted according to the heating temperature, but is made 1 second or more so as to cause softening of bainite to progress. If the heating time becomes too long, Ostwald growth of the cementite progresses and the ductility decreases, but the time can be suitably adjusted in the range of the heating temperature, so no upper limit is particularly set. Further, the time until reaching the above heating temperature or the speed of temperature rise until reaching the above heating temperature is not particularly limited.
  • the heating may be performed not only by immersion in sand, molten salt, or molten lead, which is heated at a predetermined temperature, but also by resistance heating or induction heating.
  • the conditions in the examples are just examples of conditions employed for confirming the feasibility and effects of the present invention.
  • the present invention is not limited to these examples of conditions.
  • the present invention can employ various conditions so long as not deviating from the gist of the present invention and so long as achieving the object of the present invention.
  • Wire rods of the chemical compositions A to O shown in Table 1 were held at the predetermined temperatures for the predetermined times shown in the "cooling conditions” shown in Table 2-1 to complete the bainite transformation.
  • the wire rods after the completion of the bainite transformation were respectively heated until the predetermined temperatures shown in the "heat treatment conditions after completion of bainite transformation” and held at those predetermined temperatures for predetermined times.
  • the results of measurement of the tensile strength TS (MPa) and reduction of area (%) of each of the heat treated wire rods, the results of measurement of the ratio of bainite structure and full width at half maximum of the ferrite phase in the bainite structure, and the distribution of hardness of the wire rod cross-section are shown in Table 2-2.
  • the bainite transformation time is suitably changed with an upper limit of 300 seconds when directly heat treating the hot rolled wire rods and is suitably changed with an upper limit of 1800 seconds when patenting the reheated wire rods.
  • wire rods obtained by hot rolling the billets of the chemical compositions shown in Table 1 under the conditions shown in Table 2-1 were used.
  • the wire rods of Invention Examples 1 to 3and Comparative Example 7 were produced by the method for production including the steps of producing the wire rods of the chemical compositions shown in Table 1, cooling the wire rods once and reheating the wire rods by the heating temperatures shown in Table 2-1.
  • the composition of the steel type K in Table 1 corresponds to the composition of the steel wire of PLT 3.
  • a wire rod having this composition was held at the predetermined temperature for the predetermined time of the "cooling conditions" of Table 2-1 to thereby cause progression of the bainite transformation of the wire rod of Comparative Example 6 before the bainite transformation was finished.
  • the wire rod of Comparative Example 7 was heated until the predetermined temperature shown in the "heat treatment conditions after completion of bainite transformation" and held at that predetermined temperature for a predetermined time as heat treatment to thereby finish bainite transformation.
  • EBSD electron backscatter diffraction
  • KAM kernel average misorientation
  • an X-ray diffraction apparatus was used for the full width at half maximum of the ferrite phase.
  • a Cr tubular lamp was used for the source of the X-rays.
  • the measurement surface was made the (211) plane.
  • the time when a maximum count reached 3000 or more was measured.
  • the full width at half maximum of that maximum count was made the measured value.
  • the inventors investigated in advance the correspondence between manufacturing conditions such as compositions of the types of steel and heat treatment and the ratio of bainite structure for the wire rods of Invention Examples 1 to 7 and Comparative Example 1 to 7. Based on the results of their investigations, the extent of progression of bainite transformation in the microstructure of each of the wire rods was judged, and the start and end of the bainite transformation of each of the wire rods of Invention Examples 1 to 7 and Comparative Examples 1 to 7 were judged.
  • Invention Examples 1 to 7 are working examples of the present invention. As shown in Table 2-2, bainite wire rods excellent in wire drawing characteristics are obtained.
  • Comparative Examples 2 and 3 the elements improving the hardenability, that is, Si and Mn, were respectively over the prescribed ranges and the hardenability became too high, so the transformation was not completed by the first stage of cooling.
  • Comparative Example 4 the temperature in the first stage of cooling exceeded the prescribed range, so the cooling became slower and a large amount of pearlite was formed. As a result, the targeted ratio of bainite structure could not be obtained.
  • Comparative Example 5 the heating in the second stage of cooling was not performed, so the full width at half maximum exceeded the prescribed value and the tensile strength TS did not satisfy formula (1).
  • Comparative Example 6 C exceeded the prescribed range, cementite was formed during the cooling from austenite, and the reduction of area RA did not satisfy formula (2).
  • the present invention it is possible to provide a wire rod excellent in wire drawing characteristics based on findings regarding the softening mechanism of bainite and the ratio of structures enabling reduction of the work hardening rate. Accordingly, the present invention has a high applicability in the wire rod producing industry.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
EP15759266.8A 2014-03-06 2015-03-06 High-carbon steel wire having superior wire drawing properties and method for producing same Active EP3115478B1 (en)

Applications Claiming Priority (2)

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JP2014044216 2014-03-06
PCT/JP2015/056691 WO2015133614A1 (ja) 2014-03-06 2015-03-06 伸線加工性に優れた高炭素鋼線材とその製造方法

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JP6673478B2 (ja) * 2016-07-05 2020-03-25 日本製鉄株式会社 線材、鋼線及び部品
JP6596470B2 (ja) * 2017-07-20 2019-10-23 トクセン工業株式会社 医療処置具用ワイヤ及びガイドワイヤ
CN108823490A (zh) * 2018-06-01 2018-11-16 张家港保税区恒隆钢管有限公司 一种汽车横向稳定杆无缝钢管
CN109281214A (zh) * 2018-12-03 2019-01-29 江苏兴达钢帘线股份有限公司 一种钢帘线及其制造方法及具有此钢帘线的轮胎
KR102362665B1 (ko) * 2019-12-20 2022-02-11 주식회사 포스코 선재, 고강도 강선 및 이들의 제조방법

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JP2652099B2 (ja) * 1991-10-24 1997-09-10 新日本製鐵株式会社 高強度ビードワイヤの製造方法
JP2984888B2 (ja) * 1992-06-23 1999-11-29 新日本製鐵株式会社 伸線加工性に優れた高炭素鋼線材または鋼線およびその製造方法
JP2984889B2 (ja) 1992-07-08 1999-11-29 新日本製鐵株式会社 伸線加工性に優れた高炭素鋼線材または鋼線およびその製造方法
US5647918A (en) * 1993-04-06 1997-07-15 Nippon Steel Corporation Bainite wire rod and wire for drawing and methods of producing the same
US5658399A (en) * 1993-04-06 1997-08-19 Nippon Steel Corporation Bainite wire rod and wire for drawing and methods of producing the same
JPH06306481A (ja) * 1993-04-22 1994-11-01 Nippon Steel Corp 流動層を用いた鋼線の熱処理方法
JP3018268B2 (ja) 1993-05-25 2000-03-13 新日本製鐵株式会社 伸線加工性に優れた高炭素鋼線材または鋼線およびその製造方法
JP3398207B2 (ja) * 1994-03-18 2003-04-21 新日本製鐵株式会社 伸線加工性と疲労特性の優れた冷間線引き用硬鋼線材の製造方法
JPH07268487A (ja) * 1994-04-01 1995-10-17 Nippon Steel Corp 伸線加工性に優れた高炭素鋼線材または鋼線の製造方法
JP3388418B2 (ja) * 1994-06-21 2003-03-24 新日本製鐵株式会社 伸線加工性に優れた高炭素鋼線材または鋼線の製造方法
JP2001220650A (ja) * 1999-11-30 2001-08-14 Sumitomo Electric Ind Ltd 鋼線、ばね及びそれらの製造方法
JP2002241899A (ja) * 2001-02-09 2002-08-28 Kobe Steel Ltd 耐遅れ破壊性と鍛造性に優れた高強度鋼線およびその製造方法
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EP3115478A1 (en) 2017-01-11
JP5900710B2 (ja) 2016-04-06
KR101944599B1 (ko) 2019-01-31
EP3115478A4 (en) 2017-09-06
JPWO2015133614A1 (ja) 2017-04-06
CN105980589B (zh) 2018-01-16
CN105980589A (zh) 2016-09-28
WO2015133614A1 (ja) 2015-09-11
KR20160114697A (ko) 2016-10-05

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