EP1865079A1 - Barre de fil ayant une capacité de tréfilage supérieure et sa procédé de production - Google Patents

Barre de fil ayant une capacité de tréfilage supérieure et sa procédé de production Download PDF

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Publication number
EP1865079A1
EP1865079A1 EP07252270A EP07252270A EP1865079A1 EP 1865079 A1 EP1865079 A1 EP 1865079A1 EP 07252270 A EP07252270 A EP 07252270A EP 07252270 A EP07252270 A EP 07252270A EP 1865079 A1 EP1865079 A1 EP 1865079A1
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EP
European Patent Office
Prior art keywords
wire rod
wire
exclusive
temperature
ppm
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
EP07252270A
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German (de)
English (en)
Inventor
Takeshi Kuroda
Hidenori Sakai
Tomotada Maruo
Takuya Kochi
Shogo Murakami
Hiroshi Yaguchi
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Kobe Steel Ltd
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Kobe Steel Ltd
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Publication date
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Publication of EP1865079A1 publication Critical patent/EP1865079A1/fr
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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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Definitions

  • the invention relates to a wire rod excellent in wire-drawing workability, out of which a drawn wire product, such as a steel cord, beading wire, PC steel wire, spring steel, can be efficiently produced with high productivity, and a method for producing the same.
  • a drawn wire product such as a steel cord, beading wire, PC steel wire, spring steel
  • a drawing process is applied to a wire rod serving as material for the wire product in order to make adjustment in size and quality (physical properties), and therefore, it is extremely useful from the viewpoint of enhancement in productivity, and so forth to improve wire-drawing workability of the wire rod.
  • this will not only improve productivity, due to an increase in drawing rate and a decrease in the number of drawing passes, but also provide many benefits such as reduction in wear and tear of draw dies.
  • JP-A Japanese Unexamined Patent Application Publication
  • JP-A-295930 / 1996 there has been disclosed that the wire-drawing workability is improved by controlling an area ratio of upper bainite formation, and growth size of intergranular bainite.
  • JP-A-130258/1987 there has been disclosed a technology for improving resistance to wire break, and a die life by controlling an amount of total oxygen, and nonviscous inclusion composition, in steel.
  • the invention has been developed, and it is therefore an object of the invention to provide a wire rod excellent in wire-drawing workability, insusceptible to wire break in spite of an increase in wire-drawing rate, and reduction of area, and capable of extending a die life by suppressing die wear, and a method for producing the same.
  • a wire rod that has succeeded in achieving the object is made of steel containing C: 0.6 to 1.1 % (mass %, applicable to all components referred to hereunder), Si: 0.1 to 2.0%, Mn: 0.1 to 1 %, P: not more than 0.020 % (0 % exclusive), S: not more than 0.020 % (0 % exclusive), N: not more than 0.006 % (0 % exclusive), A1: not more than 0.03 % (0 % exclusive), and 0 : not more than 0.003 % (0 % exclusive), the balance including Fe, and unavoidable impurities, and further, the wire rod comprises a pearlite structure wherein an area ratio of a second-phase ferrite is not more than 11.0 %, and a pearlite lamellar spacing is not less than 120 ⁇ m.
  • the wire rod according to the aspect of the invention may contain not more than 1.5 % Cr for higher strength, and may further contain not more than 1 % Cu, and / or not more than 1 % Ni, for suppression of decarburization.
  • the wire rod according to the aspect of the invention preferably further contains at least one element selected from the group consisting of not more than 0.30 % V, not more than 0.1 % Ti, not more than 0.10 % Nb, not more than 0.5 % Mo, and not more than 0.1 % Zr from the viewpoint of refinement of the metal microstructure, and suppression of transformation into ferrite.
  • the wire rod according to the aspect of the invention may further contain at least one element selected from the group consisting of not more than 5 ppm Mg, not more than 5 ppm Ca, and not more than 1.5 ppm REM in order to soften oxides and enhance the wire drawing workability. Still further, the wire rod according to the invention may contain not more than 15 ppm B in order to enhance hardenability.
  • a method for producing a wire rod comprising the steps of heating a steel product meeting requirements for chemical components, as described hereinbefore, to a temperature in a range of 900 to 1250°C, hot rolling the steel product at a temperature not lower than 780°C, and finish-rolling the same at a temperature not higher than 1100°C to be thereby formed into a wire rod, water-cooling the wire rod to a temperature range of 750 to 950°C before coiling the same up to be placed on conveying equipment, cooling the wire rod at an average cooling rate of not less than 20°C / sec within 20 sec from the coiling of the wire rod to thereby drop temperature of the wire rod to a minimum value point (T1) in a temperature range of 550 to 630°C, and subsequently heating the wire rod to thereby raise the temperature of the wire rod up to a maximum value point (T2) in a temperature range of 580 to 720°C, higher in temperature than T1, within 50 sec from
  • a wire rod excellent in wire-drawing workability, insusceptible to wire break, and capable of extending a die life by suppressing die wear can be obtained by specifying the respective contents of C, Si, Mn, P, S, N, Al, and O while controlling the area ratio of the second-phase ferrite and the pearlite lamellar spacing.
  • a wire rod according to the invention has features lying in requirements for chemical components thereof, and requirements for a metal microstructure thereof (an area ratio of a second-phase ferrite, and a pearlite lamellar spacing). Accordingly, the chemical components of the wire rod (a steel product) are first described hereinafter.
  • Carbon is an element intensely affecting strength of the wire rod, and in order to secure strength required of a steel cord, beading wire, PC steel wire, and so forth, as targets for which the invention has been developed, addition of not less than 0.6 % C is required. On the other hand, if carbon content is excessive, there occurs degradation in ductility, so that an upper limit of the carbon content is set to 1.1 %.
  • the carbon content is preferably in a range of 0.8 to 1.0 %.
  • Si is added to a wire rod to be subjected to intense drawing, and addition of not less than 0.1 % Si is required. Further, because Si also contributes to enhancement in strength of the wire rod due to solid solution hardening, an addition amount thereof is increased as necessary. However, an excessive increase in the strength due to excessive addition of Si will cause deterioration in wire-drawing workability. Furthermore, the excessive addition of Si will cause promotion of decarburization, to which attention should be given. For those reasons, with the invention, an upper limit of silicon content is set to 2.0 % to prevent deterioration in wire-drawing workability, and promotion of decarburization. The silicon content is preferably in a range of 0.15 to 1.8 %.
  • Mn additive of not less than 0.1 % Mn is required for the purpose of deoxidization, and locking a deleterious element S in the form of MnS to thereby render S harmless. Further, Mn also acts so as to stabilize carbide in steel. However, because excessive Mn content will cause occurrence of segregation, and supercooled structures, thereby causing deterioration in wire drawing workability, an upper limit of Mn content is set to 1 %. The Mn content is more preferably in a range of 0.15 to 0.9 %.
  • P is an element deleterious to wire drawing workability, in particular, and because excessive P content causes degradation in tenacity and ductility of a wire rod, an upper limit of P content is set to 0.020 %.
  • the P content is more preferably not more than 0.015 %, and further preferably, not more than 0.010 %.
  • S as well is an element deleterious to wire drawing workability, in particular. If Mn is contained, S can be locked in the form of MnS, as described above, however, excessive S content causes an increase in amount as well as size of MnS, thereby resulting in degradation of ductility, an upper limit of S content is set to 0.020 %.
  • the S content is more preferably not more than 0.015 %, further preferably, not more than 0.010 %.
  • N is an element contributing to an increase in strength due to age hardening.
  • Apreferable lower limit of N content is 0. 001 %.
  • an upper limit thereof is set to 0.006 %.
  • the upper limit is preferably not more than 0.004 %, more preferably, not more than 0.003 %.
  • Al is an element effective as a deoxidizer, and further, is combined with N to form AlN, which contributes to refinement of a metal microstructure.
  • a preferable lower limit of Al content is 0.0003 %. However, if the Al content is excessive, this will cause coarse oxides to be formed, thereby resulting in deterioration of wire drawing workability, and an upper limit thereof is therefore set to 0.03 %.
  • the upper limit thereof is preferably not more than 0.01 %, more preferably not more than 0.005 %.
  • an upper limit of the oxygen content is therefore set to 0.003 %.
  • the upper limit thereof is preferably not more than 0.002 %, more preferably not more than 0.0015 %.
  • the chemical components described as above represent basic components, and the balance includes in effect Fe, and unavoidable impurities, however, the wire rod may contain the following elements if needs be.
  • Cr is an element effective for rendering the wire rod higher in strength, and a preferable lower limit of Cr content is 0.01 %.
  • an upper limit of the Cr content is set to 1.5 %. The upper limit thereof is preferably not more than 1.0 %.
  • Cu is an element acting so as to enhance corrosion resistance besides acting so as to suppress decarburization in a surface layer, and therefore, Cu can be added as necessary.
  • a preferable lower limit of Cu content is 0.01 %.
  • an upper limit of the Cu content is set to 1 %. The upper limit thereof is preferably not more than 0.8 %.
  • Ni not more than 1 %
  • Ni is an element effective for suppressing decarburization in the surface layer, and enhancement in corrosion resistance, as with the case of Cu, and therefore, Ni can be added as necessary.
  • a preferable lower limit of Ni content is 0.01 %.
  • an upper limit of the Ni content is set to 1 %. The upper limit thereof is preferably not more than 0.8 %.
  • V not more than 0.30 %
  • V is an element contributing to refinement of the metal microstructure by forming carbide in carbon steel. Further, because V in solid solution state will enhance hardenability, and suppress transformation into ferrite, V can be added as necessary.
  • a preferable lower limit of V content is 0.0010 %. However, because excessive addition of V will cause deterioration in the wire drawing workability due to formation of supercooled structures, an upper limit of the V content is set to 0.3 %. The upper limit thereof is preferably not more than 0.25 %.
  • Ti is an element contributing to the refinement of the metal microstructure, and the suppression of transformation into ferrite as with the case of V, and Ti can therefore be added as necessary.
  • Apreferable lower limit of Ti content is 0.0010 %.
  • an upper limit of the Ti content is set to 0.1 %. The upper limit thereof is preferably not more than 0.08 %.
  • Nb is an element contributing to the refinement of the metal microstructure, and the suppression of transformation into ferrite as with the case of V, and Nb can therefore be added as necessary.
  • Apreferable lower limit of Nb content is 0.020 %.
  • an upper limit of the Nb content is set to 0.10 %. The upper limit thereof is preferably not more than 0.08 %.
  • Mo is an element contributing to the refinement of the metal microstructure, and the suppression of transformation into ferrite as with the case of V, and Mo can therefore be added as necessary.
  • a preferable lower limit of Mo content is 0. 05 %.
  • an upper limit of the Mo content is set to 0.5 %. The upper limit thereof is preferably not more than 0.3 %.
  • Zr is an element contributing to the refinement of the metal microstructure, and the suppression of transformation into ferrite as with the case of V, and Zr can therefore be added as necessary.
  • Apreferable lower limit of Zr content is 0.010 %.
  • an upper limit of the Zr content is set to 0.1 %. The upper limit thereof is preferably not more than 0.05 %.
  • Mg is an element acting so as to soften oxides to thereby enhance wire drawing workability, and Mg can therefore be added as necessary.
  • a preferable lower limit of Mg content is 0. 1 ppm.
  • an upper limit of the Mg content is set to 5 ppm. The upper limit thereof is preferably not more than 2 ppm.
  • Ca is an element acting so as to soften oxides as with the case of Mg, and Ca can therefore be added as necessary.
  • a preferable lower limit of Ca content is 0.3 ppm.
  • an upper limit of the Ca content is set to 5 ppm. The upper limit thereof is preferably not more than 2 ppm.
  • REM acts so as to soften oxides as with the case of Mg, and REM can therefore be added as necessary.
  • a preferable lower limit of REM content is 0.1 ppm.
  • an upper limit of the REM content is set to 1.5 ppm. The upper limit thereof is preferably not more than 0.5 ppm.
  • B is an element capable of enhancing hardenability, and addition of B enables the transformation into ferrite to be suppressed.
  • Apreferable lower limit of B content is 3 ppm.
  • an upper limit of the B content is set to 15 ppm. The upper limit thereof is preferably not more than 12 ppm.
  • the wire rod according to the invention has a feature in that the area ratio of the second-phase ferrite is not more than 11.0 %.
  • the second-phase ferrite refers to ferrite in a region without pearlite (lamellar structure of ferrite and cementite) formed therein, as indicated by respective arrows in Fig. 1 showing an SEM photograph of a cross-sectional face of the wire rod.
  • the second-phase ferrite is more specifically defined as "BCC - Fe crystal grains in a region surrounded by a boundary differing in misorientation angle by not less than 10 degrees from the periphery of the region, an area ratio of cementite present in the respective BCC - Fe crystal grains being not more than 6 %".
  • the area ratio of the second-phase ferrite refers to an area ratio (%) of the second-phase ferrite to an observed visual field of the cross-sectional face of the wire rod, magnified 500 to 1500 times by the scanning electron microscope (SEM), that is, (an area of the second-phase ferrite within the observed visual field / an area of the observed visual field in whole) x 100.
  • SEM scanning electron microscope
  • the area of the second-phase ferrite can be found by use of image analysis software, for example, ⁇ Image - Pro (Ver 4.0) ⁇ developed by Media Cybernetics.
  • a wire rod excellent in resistance to wire-break can be obtained by controlling the area ratio of the second-phase ferrite of the wire rod to not more than 11 %, preferably 10.0 %, and more preferably not more than 9 %.
  • a mechanism causing the above is not clearly known, however, the mechanism can be presumed to be as follows. The invention, however, is not to be limited in scope to the mechanism presumed as described hereunder.
  • the primary constituent of the metal microstructure thereof is pearlite, however, in general, there also exists the region of the second-phase ferrite, without pearlite formed therein. It is presumed that strain concentration occurs to the second-phase ferrite lower in strength than pearlite when drawing is applied, so that voids are prone to occur thereto. The voids each can become a starting point of wire break. Accordingly, it is reasoned that resistance to wire break can be enhanced by decreasing the second-phase ferrite that is low in strength and is susceptible to the strain concentration.
  • the wire rod according to the invention has a feature in that the same comprises a pearlite structure wherein the pearlite lamellar spacing is not less than 120 ⁇ m, preferably not less than 140 ⁇ m, and more preferably not less than 170 ⁇ m.
  • the wire rod according to the invention can at times include bainite, and / or martensite besides the second-phase ferrite, however, pearlite is the primary constituent of the metal microstructure thereof.
  • a ratio of a total area of those microconstituents is preferably not more than 5 %, more preferably not more than 2 %, and still more preferably, bainite, and martensite do not in effect exist.
  • the pearlite lamellar spacing refers to a thickness of a lamellar layer in pearlite, composed of a pair of a ferrite layer and a cementite layer, in pearlite.
  • the pearlite lamellar spacing is defined as a value of "the pearlite lamellar spacing” according to the invention.
  • the respective pearlite lamellar spacings within not less than thirty pieces of the colonies altogether are worked out, and a mean value thereof is defined as a value of "the pearlite lamellar spacing" according to the invention.
  • a mechanism whereby the resistance to the wire-break of the wire rod is enhanced if the pearlite lamellar spacing is not less than 120 ⁇ m is not clearly known, however, the mechanism can be presumed to be as follows. The invention, however, is not to be limited in scope to the mechanism presumed as described hereunder. Even if the second-phase ferrite exists in the wire rod, the strain concentration occurring to the second-phase ferrite will be mitigated in the case that a difference in strength between the second-phase ferrite and microstructure on the periphery thereof is small, so that occurrence of voids likely to cause wire-break is presumed to be checked.
  • An upper limit of the pearlite lamellar spacing is therefore preferably not more than 350 ⁇ m, more preferably not more than 300 ⁇ m, and still more preferably, not more than 280 ⁇ m.
  • a location on the cross-sectional face, adopted for observation by the SEM, in order to find "the area ratio of the second-phase ferrite", and “the pearlite lamellar spacing", is specified as a location at D / 4 on the cross-sectional face of the wire rod (D: diameter of the wire rod).
  • D diameter of the wire rod.
  • the wire rod according to the invention can be produced by, for example, a method described hereinafter (refer to Fig. 3).
  • the wire rod according to the invention is not limited to that produced by the method described hereinafter.
  • a steel product meeting the requirements for the chemical components is heated up to 900 to 1250°C to be subsequently hot rolled at a temperature not lower than 780°C, and a finish-rolling temperature is controlled to not higher than 1100°C. This is because heating is insufficient with a heating temperature lower than 900°C, and conversely, if the heating temperature exceeds 1250°C, decarburization in the surface layer spreads, so that scales capable of adversely affecting the wire-drawing workability tend to become harder to peel off.
  • a rolling temperature is lowered, decarburization in the surface layer is similarly promoted, and a lower limit temperature for hot rolling is therefore set to 780°C.
  • a finish-rolling temperature exceeds 1100°C, this will render it difficult to control transformation of the metal microstructure by cooling and reheating, to be executed in a subsequent process step, so that an upper limit of the finish-rolling temperature is set to 1100°C.
  • a wire rod formed after the finish-rolling is water-cooled to a temperature range of 750 to 950°C, and is coiled up on conveying equipment, such as a Stelmor conveyer, to be then placed thereon.
  • Temperature control executed after water-cooling is important for control of the transformation of the metal microstructure, taking place thereafter, and control of scales. If an ultimate temperature at the time of water-cooling is below 750°C, this will at times cause the supercooled structures to be formed in the surface layer, thereby adversely affecting the wire-drawing workability, and on the other hand, if the ultimate temperature exceeds 950°C, this will cause loss in deformability of scales, so that scales will peel off in the course of transportation, thereby creating a cause for rusting.
  • a reference time for "within 20 sec from the coiling" is a point in time when a rolled wire rod is coiled up in ring-like fashion to be placed on the conveying equipment, such as the conveyer. Further, since the wire rod is continuously coiled up, and is continuously cooled, there occurs time lag between the top part of the wire rod, coiled up, and the bottom part thereof, to be coiled up, with respect to a time when the wire rod is placed, and a time when the wire rod is cooled, respectively, however, respective measurements on time from the coiling up to the cooling are started upon the coiling of the respective part of the wire rod.
  • the second-phase ferrite prone to undergo strain concentration is formed at a relatively high temperature before pearlite transformation
  • formation of the second-phase ferrite can be suppressed by rapidly cooling the wire rod at the average cooling rate of not less than 20°C / sec down to a temperature region where ferrite is hard to be formed within 20 sec from the coiling of the wire rod.
  • the average cooling rate of not less than 20°C / sec down to a temperature region where ferrite is hard to be formed within 20 sec from the coiling of the wire rod.
  • advantageous effect of the metal microstructure being micronized can be gained.
  • a cooling rate is excessively high, this will raise the risk of an increase in strength differential within the wire rod, due to localized formation of supercooled structures, and so forth, thereby causing deterioration in the wire drawing workability.
  • the average cooling rate is preferably set to not more than 50°C / sec.
  • the average cooling rate refers to a cooling rate found on the basis of a temperature difference between the wire rod temperature upon the coiling thereof (that is, the wire rod temperature after water-cooling) and T1, and a cooling time length required for the wire rod temperature at the time of the coiling to drop down to T1.
  • the wire rod is cooled down only to the minimum value point (T1) in excess of 630°C in such a cooling process step as described above, it is not possible to sufficiently suppress the formation of the second-phase ferrite, so that coarse grains having adverse effects on the wire-drawing workability become prone to be easily formed.
  • the wire rod is excessively cooled down to the minimum value point (T1) below 550°C, this will lead to an increase in strength differential within the wire rod, due to the formation of the supercooled structures, and so forth.
  • the wire rod After the wire rod is cooled down to T1 in the temperature range during the cooling process step, the wire rod is reheated to thereby cause the pearlite transformation to occur.
  • the wire rod temperature By increasing the wire rod temperature to a high temperature at 580°C or higher, the pearlite lamellar spacing can be rendered wider. Further, it is presumed that the higher a transformation temperature, the wider the pearlite lamellar spacing can become, however, ductility becomes excessively low at the transformation temperature in excess of 720°C, raising the risk of the wire drawing workability undergoing deterioration contrary to expectation.
  • the pearlite lamellar spacing can be rendered wider by slowly cooling the wire rod as usual, or holding the wire rod at a constant temperature without rapidly cooling the same after the coiling thereof on the conveying equipment.
  • the metal microstructure becomes coarser because a rate at which the pearlite transformation nuclei are formed is low in a high temperature region, thereby causing adverse effects on the wire drawing workability.
  • the wire rod whose metal microstructure is fine, and has a wide pearlite lamellar spacing can be provided by a production method according to the invention, comprising a step of rapidly cooling a wire rod once after coiling thereof on a conveying equipment before reheating the same, thereby causing pearlite transformation to proceed in a high temperature region.
  • the wire rods each were water-cooled to a temperature in a range of 798 to 948°C, and were subsequently coiled up and placed on the Stelmor conveyer (a cooling bed) to be continuously cooled.
  • temperature of the wire rod was lowered to the minimum value point (T1) in a temperature range of 515 to 682°C within 20 sec from the coiling of the wire rod.
  • An average cooling rate during this time period was in a range of 13 to 99°C / sec.
  • the temperature of the wire rod was raised from T1 up to the maximum value point (T2) in a temperature range of 584 to 705°C. Further, some of the wire rods were continuously and slowly cooled from T1 without being heated up from T1.
  • the area ratio of the second-phase ferrite, and the pearlite lamellar spacing were measured as follows:
  • Wire-drawing under the respective wire-drawing conditions was applied to 50 tons each of the wire rods, and evaluation was made on whether or not a wire-break occurs, and an extent of die-wear, as criteria for the wire drawing workability.
  • symbol (X) indicates the case where any of the dies were broken in the course of wire-drawing
  • symbol ( ⁇ ) indicates the case where none of the dies were broken in the course of drawing 50 tons each of the wire rods, but the dies were worn out, requiring replacement after the wire-drawing
  • symbol (O) indicates the case where none of the dies were broken, and there is no necessity of replacing the dies, due to the wear thereof, after the wire-drawing of 50 tons each of the wire rods.
  • the remaining metal microstructure is, in effect, pearlite; the metal microstructure of the wire rod No. 23: 94 % pearlite, 5 % martensite; the metal microstructure of the wire rod No. 27: 93.1 % pearlite, 3 % martensite
  • the wire rod with excellent resistance to wire-break, causing little die-wear, and excelling in the wire-drawing workability can be obtained by adequately controlling the requirements for the metal microstructure thereof (the area ratio of the second-phase ferrite, and the pearlite lamellar spacing) and the requirements for the chemical components thereof.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Metal Extraction Processes (AREA)
  • Metal Rolling (AREA)
EP07252270A 2006-06-06 2007-06-06 Barre de fil ayant une capacité de tréfilage supérieure et sa procédé de production Withdrawn EP1865079A1 (fr)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP2006157622A JP2007327084A (ja) 2006-06-06 2006-06-06 伸線加工性に優れた線材およびその製造方法

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EP1865079A1 true EP1865079A1 (fr) 2007-12-12

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EP07252270A Withdrawn EP1865079A1 (fr) 2006-06-06 2007-06-06 Barre de fil ayant une capacité de tréfilage supérieure et sa procédé de production

Country Status (7)

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US (1) US20070277913A1 (fr)
EP (1) EP1865079A1 (fr)
JP (1) JP2007327084A (fr)
KR (1) KR20070116731A (fr)
CN (1) CN101086052A (fr)
BR (1) BRPI0702592A (fr)
TW (1) TW200823300A (fr)

Cited By (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102009010442A1 (de) * 2009-02-26 2010-09-02 C.D. Wälzholz GmbH Mikrolegierter Kohlenstoffstahl als texturgewalzter Bandstahl, insbesondere für Federelemente
EP2634280A1 (fr) * 2010-10-29 2013-09-04 Kabushiki Kaisha Kobe Seiko Sho Fil-machine d'acier riche en carbone présentant une excellente aptitude à l'étirage du fil
EP2687619A1 (fr) * 2011-03-14 2014-01-22 Nippon Steel & Sumitomo Metal Corporation Matériau de fil-machine et procédé pour sa production
EP2824205A1 (fr) * 2012-03-07 2015-01-14 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Tige de fil d'acier présentant une excellente aptitude au façonnage en ressort pour un ressort à résistance élevée, son procédé de fabrication, et ressort à résistance élevée
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WO2010097078A3 (fr) * 2009-02-26 2010-12-23 C.D. Wälzholz GmbH Acier au carbone microallié pour former un feuillard laminé texturé, en particulier pour des éléments élastiques
US9290832B2 (en) 2009-02-26 2016-03-22 C.D. Waelzholz Gmbh Micro-alloyed carbon steel as a texture-rolled strip steel, in particular for spring elements
DE102009010442A1 (de) * 2009-02-26 2010-09-02 C.D. Wälzholz GmbH Mikrolegierter Kohlenstoffstahl als texturgewalzter Bandstahl, insbesondere für Federelemente
US9121080B2 (en) 2010-04-01 2015-09-01 Kobe Steel, Ltd. High-carbon steel wire excellent in wire drawability and fatigue property after wiredrawing
EP2634280A1 (fr) * 2010-10-29 2013-09-04 Kabushiki Kaisha Kobe Seiko Sho Fil-machine d'acier riche en carbone présentant une excellente aptitude à l'étirage du fil
US9994940B2 (en) 2010-10-29 2018-06-12 Kobe Steel, Ltd. High carbon steel wire rod having excellent drawability
EP2634280A4 (fr) * 2010-10-29 2014-04-02 Kobe Steel Ltd Fil-machine d'acier riche en carbone présentant une excellente aptitude à l'étirage du fil
US9255306B2 (en) 2011-03-14 2016-02-09 Nippon Steel & Sumitomo Metal Corporation Steel wire rod and method of producing same
EP2687619A1 (fr) * 2011-03-14 2014-01-22 Nippon Steel & Sumitomo Metal Corporation Matériau de fil-machine et procédé pour sa production
EP2687619A4 (fr) * 2011-03-14 2014-11-26 Nippon Steel & Sumitomo Metal Corp Matériau de fil-machine et procédé pour sa production
EP2824205A1 (fr) * 2012-03-07 2015-01-14 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Tige de fil d'acier présentant une excellente aptitude au façonnage en ressort pour un ressort à résistance élevée, son procédé de fabrication, et ressort à résistance élevée
EP2824205A4 (fr) * 2012-03-07 2015-08-26 Kobe Steel Ltd Tige de fil d'acier présentant une excellente aptitude au façonnage en ressort pour un ressort à résistance élevée, son procédé de fabrication, et ressort à résistance élevée
EP2832891A4 (fr) * 2012-03-30 2016-04-27 Kobe Steel Ltd Tige de fil d'acier avec une excellente capacité d'égalisation pour ressort haute résistance, et ressort haute résistance
US20150203943A1 (en) * 2012-10-19 2015-07-23 Nippon Steel & Sumitomo Metal Corporation Steel for induction hardening with excellent fatigue properties
US9896749B2 (en) * 2012-10-19 2018-02-20 Nippon Steel & Sumitomo Metal Corporation Steel for induction hardening with excellent fatigue properties
EP3072987A4 (fr) * 2013-11-22 2017-06-07 Nippon Steel & Sumitomo Metal Corporation Tôle en acier à teneur élevée en carbone et son procédé de production
US10407748B2 (en) 2013-11-22 2019-09-10 Nippon Steel Corporation High-carbon steel sheet and method of manufacturing the same
EP3109335A4 (fr) * 2014-02-11 2017-10-04 Institute Of Research Of Iron And Steel, Jiangsu Province/Sha-Steel, Co., Ltd Tige de fil d'acier à haute teneur en carbone et son procédé de préparation
US10316386B2 (en) 2014-02-11 2019-06-11 Institute of Research of Iron and Steel, Jiangsu Province/Sha-Steel, Co. Ltd. High-carbon steel wire rod and preparation method therefor
EP3150738A4 (fr) * 2014-06-02 2018-01-24 Nippon Steel & Sumitomo Metal Corporation Matériau de fil d'acier
EP3282027A4 (fr) * 2015-03-30 2018-09-05 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Matériau de fil d'acier à haute teneur en carbone présentant une excellente aptitude à l'étirage de fil et fil d'acier

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US20070277913A1 (en) 2007-12-06
JP2007327084A (ja) 2007-12-20

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