EP2025769A1 - Stark dehnbarer hartstahldraht - Google Patents

Stark dehnbarer hartstahldraht Download PDF

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Publication number
EP2025769A1
EP2025769A1 EP07744836A EP07744836A EP2025769A1 EP 2025769 A1 EP2025769 A1 EP 2025769A1 EP 07744836 A EP07744836 A EP 07744836A EP 07744836 A EP07744836 A EP 07744836A EP 2025769 A1 EP2025769 A1 EP 2025769A1
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EP
European Patent Office
Prior art keywords
wire rod
carbon steel
steel wire
pearlite
less
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Withdrawn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
EP07744836A
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English (en)
French (fr)
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EP2025769A4 (de
Inventor
Seiki Nishida
Shingo Yamasaki
Hitoshi Demachi
Nariyasu Muroga
Shouichi Ohashi
Kenichi Nakamura
Makoto Kosaka
Nobuyuki Komiya
Susumu Sahara
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
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Nippon Steel Corp
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Filing date
Publication date
Application filed by Nippon Steel Corp filed Critical Nippon Steel Corp
Publication of EP2025769A1 publication Critical patent/EP2025769A1/de
Publication of EP2025769A4 publication Critical patent/EP2025769A4/de
Withdrawn legal-status Critical Current

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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
    • 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
    • C22C38/002—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • D—TEXTILES; PAPER
    • D07—ROPES; CABLES OTHER THAN ELECTRIC
    • D07B—ROPES OR CABLES IN GENERAL
    • D07B1/00—Constructional features of ropes or cables
    • D07B1/06—Ropes or cables built-up from metal wires, e.g. of section wires around a hemp core
    • D07B1/0606—Reinforcing cords for rubber or plastic articles
    • D07B1/066—Reinforcing cords for rubber or plastic articles the wires being made from special alloy or special steel composition
    • 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

Definitions

  • This invention relates to high-carbon steel wire rod of high post-hot-rolling ductility having a metallographic structure mainly of pearlite. Specifically, this invention relates to piano wire or high-carbon steel wire complying with JIS, more particularly to hot-rolled wire of high-carbon steel that, as the final product steel wire, is a fine wire of a diameter of around 0.1 to 2 mm usable, for example, in steel cord, saw wire, hose wire, fine rope and the like.
  • Steel cords and other reinforcing wires used to reinforce rubber products such as tires, conveyor belts and heavy-duty hoses are manufactured from high-carbon steel wire rods.
  • the high-carbon steel wire rods are manufactured by hot rolling, followed by descaling and then borax coating or Bonde coating to provide a carrier coating, whereafter processing to a steel wire of 0.8 to 1.2 mm is optionally conducted by use of intermediate patenting.
  • the hot-rolled steels are called “wire rods” and the steels of smaller diameter than the hot-rolled steels fabricated by subsequent processing are called “steel wires.”
  • This wire rod is directed to enabling the drawing dice to have excellent service life and increases dice service life by specifying tensile strength and controlling the volume fraction of coarse pearlite to within a certain range.
  • Japanese Patent Publication (A) No. 2000-6810 teaches a high-carbon steel wire rod excellent in wire drawability wherein 90% or greater of the metallographic structure is pearlite structure, and the pearlite has an average lamellar spacing of 0.1 to 0.4 ⁇ m and an average colony diameter of 150 ⁇ m or less.
  • the fact is, however, that the colony diameter obtained by ordinary hot rolling is smaller than 150 ⁇ m, and an improvement in breakage property cannot necessarily be expected because the ductility obtained when the colony diameter is controlled to 150 ⁇ m or less is inconsistent.
  • the invention taught by this patent publication controls the lamellar spacing and nodule size by incorporating a cooling process for isothermal holding during Stelmor cooling at the time of hot rolling.
  • the cooling is continuous, so that the range of lamellar spacing values is wide and the range of nodule size values also becomes wide.
  • good workability cannot be obtained no matter how small the average values are made, and what is more, a problem of attendant internal defects arises.
  • the patented invention is directed to obtaining a wire rod excellent in high-speed drawability by varying the cooling conditions after wire rod rolling so as to adjust the structure into the range of F defined by the foregoing equation. This is problematic, however, because bringing the structure into the range of the equation requires use of special heat treatment that is generally difficult to implement.
  • the present invention relates to high-carbon steel wire rod utilized as piano wire rod, hard steel wire rod and the like for use in finely drawn applications such as steel cord, belt cord, rubber hose wire, rope wire and the like, and in light of the foregoing circumstances, provides high-carbon steel wire rod of high ductility that is excellent in post-hot-rolling drawability, resists occurrence of internal defects at the time of drawing, and enables omission of intermediate patenting.
  • the inventors achieved the present invention based on the results of in-depth research regarding pearlite structure hot-rolled wire rod whose secondary processability is unaffected by omission of intermediate patenting.
  • a summary of the invention follows:
  • the inventors observed the internal defect sites after primary drawing and studied the associated conditions, which are complexly affected by numerous factors such as the mechanical properties, processing conditions and wire rod structure. As a result, they discovered that among these conditions, it is the pearlite block size of the pearlite structure at the core of the wire rod, as measured with an EBSP (Electron Back Scatter Pattern) analyzer, that characterizes the structure readily experiencing internal defects.
  • EBSP Electro Back Scatter Pattern
  • Pearlite block size was measured with a system using a TSL (TexSEM Laboratories) EBSP analysis unit in combination with a Hitachi thermal FE-SEM (model S-4300SE).
  • the pearlite block was measured with the EBSP analyzer as the region with the same ferrite crystal orientation, in accordance with the definition given by Takahashi et al. in The Journal of the Japan Institute of Metals, Vol. 42 (1978), p702 . Since measurement using the structure observed with a light microscope or the secondary electron image obtained by SEM observation was found to be extremely difficult, the pearlite block size was determined from the ferrite crystal orientation map obtained by EBSP analysis. Differently from in the ferrite single phase of low-carbon steel, countless small angle boundaries are present in the ferrite crystal grains of pearlite steel, even after patenting.
  • the inventors discovered that occurrence of coarse pearlite blocks can be prevented by control of oxygen amount along with control of post-rolling finish-rolling temperature so as to carry out Stelmor cooling with the ⁇ grain size in a granulated state on the finish rolling exit side.
  • the ⁇ grains are of mixed grain size, pearlite transformation occurs more readily at small ⁇ grain regions, in which case the pearlite transformation nuclei are present heterogeneously, so that pearlite blocks grow easily to make the grain size large.
  • the steel In order to make the ⁇ grain size after finish rolling small, the steel is required to have an oxygen content of 18 ppm or greater, preferably 20 ppm or greater. However, increasing oxygen content increases the amount of inclusions and causes formation of large inclusions. As this degrades ductility, the upper limit of oxygen content is defined as 30 ppm.
  • the pearlite block size varies from the surface layer toward the center of the wire rod. And, as shown in FIG. 2 , the pearlite block size varies at locations outward from the center also in the case where the ordinary Stelmor cooling process is conducted.
  • each pearlite block size shown is the average of values measured at eight locations. Since the pearlite block size at the core differs greatly even when the average value is the same, the inventors studied what criteria should be used for the control in the case of continuous cooling. They learned that the pearlite lamellae are also coarse at the core region where the pearlite block size is large and that the coarse pearlite portions become starting points of breakage during drawing.
  • the pearlite block grains are present in a mixture of sizes. If the average pearlite block size is determined by simple averaging based on the measurement of pearlite block size made in this mixed condition, the numerous small pearlite blocks present will make the average value so small that it does not reflect the breakage property.
  • the Johnson-Saltykov method of calculating the average diameter of particle groups of mixed particle size was therefore used to determine the average value of the obtained pearlite block size as the average of values at 8 sites in each of the wire rod surface layer, 1/4 diameter region and core region (1/2 diameter region), i.e., at a total of 24 sites. Details regarding the Johnson-Saltykov method can be found in Quantitative Microscopy, R.T. DeHoff and F.N. Rhines, Ed., McGraw Hill Publishers, New York, NY, 1968, p169 .
  • the obtained average value is 10 ⁇ m or less
  • achievement of pearlite structure of 95% or greater is difficult and the volume percentage of ferrite in the pearlite structure becomes 2% or greater.
  • the average pearlite block size therefore needs to be made 10 ⁇ m or greater.
  • the probability of coarse blocks being included is very high in the case of continuous cooling, so that the average must be controlled to 30 ⁇ m or less.
  • Reduction of area is preferably controlled to not less than ⁇ 72.8 - 40 x (C mass%) ⁇ .
  • the volume fraction of pro-eutectoid ferrite observed inside the wire rod obtained by Stelmor cooling is controlled to 2% or less.
  • the pro-eutectoid ferrite tends to act as starting points of internal defects during drawing and as starting points of internal defects during tensile testing.
  • Pro-eutectoid ferrite is therefore controlled to 2% or less.
  • Pro-eutectoid ferrite becomes a problem in the carbon content region below 0.85 mass%. In the carbon content region of 0.85 mass% and greater, pro-eutectoid ferrite is generally held to 2% or less owing to the presence of abundant carbon content.
  • C is an element that effectively enhances strength.
  • C content For obtaining a high-strength steel wire, C content must be made 0.7% or greater. However, when C content is excessive, ductility tends to be lowered by ready precipitation of pro-eutectoid cementite. The upper limit of C content is therefore specified as 1.1%.
  • Si is an element required for deoxidation of the steel. Since the deoxidation effect is insufficient at too low a content, Si is added to a content of 0.1% or greater. Moreover, Si increases post-patenting strength by dissolving into the ferrite phase in the pearlite formed after heat treatment. But it also impairs heat treatability. It is therefore kept to a content of 1.0% or less.
  • P easily segregates and P concentrating at the segregation sites dissolves into the ferrite to lower workability. P content is therefore controlled to 0.02% or less.
  • Mn is added to a content of 0.1% or greater in order to impart hardenability to the steel.
  • heavy addition of Mn excessively prolongs transformation time during patenting. Addition is therefore limited to 1.0% or less.
  • Cr is added to enhance steel strength. When included, it is added to a content at which this effect is exhibited, namely to a content of 0.05% or greater, and to a content of 1.0% or less, namely to a content that does not give rise to a decrease in steel wire ductility.
  • Mo is added to enhance steel strength. When included, it is added to a content at which this effect is exhibited, namely to a content of 0.05% or greater, and to a content of 1.0% or less, namely to a content that does not give rise to a decrease in steel wire ductility.
  • Cu is added to enhance corrosion resistance and corrosion fatigue property. When included, it is added to a content at which these effects are manifested, namely to a content of 0.05% or greater. However, heavy addition tends to cause brittleness during hot rolling, so the upper limit is defined as 1.0%.
  • Ni has an effect of increasing steel strength. When included, it is added to a content at which the effect of addition is manifested, namely to a content of 0.05% or greater. However, since excessive addition lowers ductility, Ni content is held to 1.0% or less.
  • V has an effect of increasing steel strength. When included, it is added to a content at which the effect of addition is manifested, namely to a content of 0.001% or greater. However, excessive addition lowers ductility, so the upper limit is defined as 0.1%.
  • Nb has an effect of increasing steel strength. When included, it is added to a content at which the effect of addition is manifested, namely to a content of 0.001% or greater. However, excessive addition lowers ductility, so the upper limit is defined as 0.1%.
  • B has an effect of refining ⁇ grain size during austenitization, and by this, of improving reduction and other ductility properties. Therefore, when included, B is added to a content at which its effect is manifested, namely to a content of 0.0005% or greater. However, addition to a content exceeding 0.006% makes the transformation time at the time that transformation is effected by heat treatment too long. The upper limit of B content is therefore defined as 0.006%.
  • the production method for obtaining the high-carbon steel wire rod of high ductility it is preferable in hot rolling a billet having the aforesaid chemical composition to conduct the hot rolling at a hot finish temperature of 800 °C or greater and 1050 °C or less, then carry out coiling at 800 to 830 °C within 10 seconds, and thereafter conduct Stelmor cooling or direct patenting by immersion in 500 to 570 °C molten salt.
  • the chemical compositions of specimen steels used in prototyping are shown Table 1.
  • Steels No. 1 to No. 18 are of compositions controlled in accordance with the invention.
  • Steels No. 19 and No. 20 are Comparative Steels. Comparative Steel 19 is lower in oxygen content than the Invention Steels and Comparative Steel 20 is higher in oxygen content than the Invention Steels.
  • the steels were prepared in a full-scale furnace to have the compositions shown in Table 2 and continuously cast into bloom of 500 x 300 mm cross-sectional dimensions.
  • the bloom was thereafter reheated and rolled with a billeting mill to obtain a 122 mm-square billet.
  • the steel was then reheated to the ⁇ region, hot rolled to 5.5 mm-diameter wire rod, finish rolled, controlled to a coiling temperature of 850 to 900 °C in 10 seconds, and continuously subjected to Stelmor cooling divided into four zones.
  • the wire rod manufacturing conditions are shown in Table 2.
  • Table 2 also shows the mechanical properties and the maximum and average values of the measured pearlite block sizes of the wire rods obtained under the manufacturing conditions shown in the same Table.
  • Wire rods No. 1, No. 2 and, No. 6 to No. 21 in Table 2 were manufactured in accordance with the invention.
  • Wire rods No. 3 to No. 5, No. 22 and No. 23 were manufactured for comparison.
  • the symbol ⁇ indicates that when, for the purpose of investigating primary drawability, the wire rod was drawn from the diameter of 5.5 mm to a diameter of 1.0 mm with the die approach angle at 20 degrees, neither breakage nor abnormality in the tensile tests conducted at the individual passes occurred.
  • the wire rod was drawn from the diameter of 5.5 mm to a diameter of 1.56 mm, brass plated and further drawn from the diameter of 1.56 mm to a diameter of 0.2 mm, whereafter the 0.2 mm-diameter wire was subjected to drawing under a weight of 100 kg or greater to determine the wire breakage index.
  • the wire breakage index was good, it was designated by the symbol ⁇ .
  • the symbol X indicates that the result for the item concerned was unsatisfactory.
  • the invention wire rods No. 1, No. 2, and No. 6 to No. 21 exhibited good results for both primary drawability and secondary drawability.
  • Comparative wire rod No. 3 made with a comparative steel, had a maximum pearlite block size value exceeding 65 ⁇ m owing to the high finishing temperature and therefore exhibited poor results for both primary drawability and secondary drawability.
  • Comparative wire rod No. 4 had a maximum pearlite block size value exceeding 65 ⁇ m owing to the high coiling temperature and therefore exhibited poor results for both primary drawability and secondary drawability.
  • Comparative wire rod No. 5 had a tensile strength (TS) below the invention range because the air flow in Stelmor cooling was at a moderate level. In this case, too, poor results were exhibited for both primary drawability and secondary drawability.
  • TS tensile strength
  • Comparative wire rod No. 22 was made of a steel of a chemical composition whose oxygen content was below the invention range.
  • the maximum value of the pearlite block size at the core region of the wire rod was greater than that defined by the invention.
  • Comparative wire rod No. 23 was made of a steel of a chemical composition whose oxygen content was below the invention range. Although the maximum value of the pearlite block size at the core region of the wire rod met the requirement of the invention, the total amount of inclusions was large owing to the high oxygen content and the secondary drawability was therefore low. Table 1 Steel No.
  • the high-carbon steel wire rod of high ductility enables manufacture of excellent extra fine wire of high fatigue strength that is capable of reducing the weight and prolonging the service life of rubber products.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
EP07744836A 2006-06-01 2007-05-31 Stark dehnbarer hartstahldraht Withdrawn EP2025769A4 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2006153303 2006-06-01
PCT/JP2007/061497 WO2007139234A1 (ja) 2006-06-01 2007-05-31 高延性の高炭素鋼線材

Publications (2)

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EP2025769A1 true EP2025769A1 (de) 2009-02-18
EP2025769A4 EP2025769A4 (de) 2010-08-18

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EP07744836A Withdrawn EP2025769A4 (de) 2006-06-01 2007-05-31 Stark dehnbarer hartstahldraht

Country Status (8)

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US (2) US20090087336A1 (de)
EP (1) EP2025769A4 (de)
JP (1) JP5092749B2 (de)
KR (1) KR101018054B1 (de)
CN (1) CN101341270B (de)
BR (1) BRPI0702892B1 (de)
CA (1) CA2617381C (de)
WO (1) WO2007139234A1 (de)

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CN103415637A (zh) * 2011-03-01 2013-11-27 新日铁住金株式会社 拉丝性和拉丝后的疲劳特性优异的高碳钢线材
EP2687619A1 (de) * 2011-03-14 2014-01-22 Nippon Steel & Sumitomo Metal Corporation Stahldrahtmaterial und herstellungsverfahren dafür
EP2905353A4 (de) * 2012-10-04 2016-03-30 Nippon Steel & Sumitomo Metal Corp Geformter stahldraht für unterwasserkabelschutzrohr, herstellungsverfahren dafür und druckbeständige schicht
EP3165626A4 (de) * 2014-08-08 2018-03-28 Nippon Steel & Sumitomo Metal Corporation Hartstahldraht mit hervorragender drahtziehbarkeit

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JP5154694B2 (ja) * 2009-11-05 2013-02-27 新日鐵住金株式会社 加工性に優れた高炭素鋼線材
BR112013004944A2 (pt) * 2010-08-30 2016-08-16 Kobe Steel Ltd vergalhão de arame de aço para mola de alta resistência excelente na capacidade de trefilação do arame, método de fabricação para ele e mola de alta resistência
JP5425744B2 (ja) 2010-10-29 2014-02-26 株式会社神戸製鋼所 伸線加工性に優れた高炭素鋼線材
JP5733120B2 (ja) * 2011-09-09 2015-06-10 住友電気工業株式会社 ソーワイヤおよびそれを用いたｉｉｉ族窒化物結晶基板の製造方法
JP5590256B2 (ja) 2012-01-20 2014-09-17 新日鐵住金株式会社 圧延線材、及びその製造方法
JP5796781B2 (ja) * 2012-03-07 2015-10-21 株式会社神戸製鋼所 ばね加工性に優れた高強度ばね用鋼線材およびその製造方法、並びに高強度ばね
JP6180351B2 (ja) 2013-03-28 2017-08-16 株式会社神戸製鋼所 生引き性に優れた高強度鋼線用線材および高強度鋼線
CN104032222B (zh) * 2014-06-24 2016-04-06 燕山大学 纳米珠光体钢轨的制备方法
JP2016014168A (ja) 2014-07-01 2016-01-28 株式会社神戸製鋼所 鋼線用線材および鋼線
CN104233097B (zh) * 2014-09-03 2017-02-15 马钢(集团)控股有限公司 制造智能坚强电网高强度钢绞线用热轧盘条及其生产方法
US10287660B2 (en) 2014-10-20 2019-05-14 Nippon Steel & Sumitomo Metal Corporation Steel wire rod for bearings having excellent drawability and coil formability after drawing
CN105063508B (zh) * 2015-08-26 2017-01-18 武汉钢铁(集团)公司 含硼高端帘线钢及其生产方法
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CN113740336B (zh) * 2021-09-03 2024-03-12 广东韶钢松山股份有限公司 一种直接获得连铸坯边部增碳的评价方法
CN114150221A (zh) * 2021-11-26 2022-03-08 湖南华菱湘潭钢铁有限公司 一种超高强钢82b的生产方法
WO2023162615A1 (ja) * 2022-02-22 2023-08-31 住友電気工業株式会社 鋼線
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CN115161558B (zh) * 2022-07-12 2024-04-16 鞍钢股份有限公司 一种超高强度钢丝帘线用盘条、钢丝、帘线及制造方法
CN117845137A (zh) * 2024-01-08 2024-04-09 钢铁研究总院有限公司 一种Mn-Si-V-Ti-Nb-Cr多元合金化热轧盘条及其制备方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5458699A (en) * 1993-05-13 1995-10-17 Sumitomo Metal Industries, Ltd. Steel wire for making high strength steel wire product and method for manufacturing thereof
US20030079815A1 (en) * 2001-06-28 2003-05-01 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) High-carbon steel wire rod with superior drawability and method for production thereof
JP2007131944A (ja) * 2005-10-12 2007-05-31 Nippon Steel Corp 伸線特性に優れた高強度線材およびその製造方法
EP1900837A1 (de) * 2005-06-29 2008-03-19 Nippon Steel Corporation Hochfester walzdraht mit hervorragender drahtziehleistungsfähigkeit und herstellungsverfahren dafür
EP2062991A1 (de) * 2007-01-31 2009-05-27 Nippon Steel Corporation Abgeflachter stahldraht für pws mit hervorragenden drehungseigenschaften sowie herstellungsverfahren dafür

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS59185730A (ja) 1983-04-07 1984-10-22 Nippon Steel Corp ダイス寿命にすぐれた改良熱間圧延線材
JPS61261436A (ja) * 1985-05-15 1986-11-19 Kawasaki Steel Corp 加工性に優れた高強度高延性線材の製造方法
JP3978555B2 (ja) 1998-06-25 2007-09-19 西日本旅客鉄道株式会社 保守用車の走行切換装置
CN1104508C (zh) * 1999-06-16 2003-04-02 新日本制铁株式会社 具有优良拉拔性能和拉拔后疲劳抗力的高碳钢线材
JP3965010B2 (ja) * 1999-12-22 2007-08-22 新日本製鐵株式会社 高強度直接パテンティング線材およびその製造方法
JP2001181789A (ja) * 1999-12-22 2001-07-03 Nippon Steel Corp 伸線加工性に優れた細径高炭素鋼熱間圧延線材
CN1117171C (zh) * 1999-12-22 2003-08-06 新日本制铁株式会社 高强度直接铅淬火线材及其制造方法
JP3681712B2 (ja) * 2001-06-28 2005-08-10 株式会社神戸製鋼所 伸線性に優れた高炭素鋼線材およびその製造方法
JP3997867B2 (ja) * 2002-09-04 2007-10-24 住友金属工業株式会社 鋼線材とその製造法及び当該鋼線材を用いる鋼線の製造法
JP4088220B2 (ja) * 2002-09-26 2008-05-21 株式会社神戸製鋼所 伸線前の熱処理が省略可能な伸線加工性に優れた熱間圧延線材

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5458699A (en) * 1993-05-13 1995-10-17 Sumitomo Metal Industries, Ltd. Steel wire for making high strength steel wire product and method for manufacturing thereof
US20030079815A1 (en) * 2001-06-28 2003-05-01 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) High-carbon steel wire rod with superior drawability and method for production thereof
EP1900837A1 (de) * 2005-06-29 2008-03-19 Nippon Steel Corporation Hochfester walzdraht mit hervorragender drahtziehleistungsfähigkeit und herstellungsverfahren dafür
JP2007131944A (ja) * 2005-10-12 2007-05-31 Nippon Steel Corp 伸線特性に優れた高強度線材およびその製造方法
EP2090671A1 (de) * 2006-10-12 2009-08-19 Nippon Steel Engineering Corporation Zugstange mit hervorragender tiefziehfähigkeit und hoher festigkeit sowie herstellungsverfahren
EP2062991A1 (de) * 2007-01-31 2009-05-27 Nippon Steel Corporation Abgeflachter stahldraht für pws mit hervorragenden drehungseigenschaften sowie herstellungsverfahren dafür

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of WO2007139234A1 *

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103415637A (zh) * 2011-03-01 2013-11-27 新日铁住金株式会社 拉丝性和拉丝后的疲劳特性优异的高碳钢线材
CN103415637B (zh) * 2011-03-01 2014-08-06 新日铁住金株式会社 拉丝性和拉丝后的疲劳特性优异的高碳钢线材
EP2687619A1 (de) * 2011-03-14 2014-01-22 Nippon Steel & Sumitomo Metal Corporation Stahldrahtmaterial und herstellungsverfahren dafür
EP2687619A4 (de) * 2011-03-14 2014-11-26 Nippon Steel & Sumitomo Metal Corp Stahldrahtmaterial und herstellungsverfahren dafür
US9255306B2 (en) 2011-03-14 2016-02-09 Nippon Steel & Sumitomo Metal Corporation Steel wire rod and method of producing same
EP2905353A4 (de) * 2012-10-04 2016-03-30 Nippon Steel & Sumitomo Metal Corp Geformter stahldraht für unterwasserkabelschutzrohr, herstellungsverfahren dafür und druckbeständige schicht
EP3165626A4 (de) * 2014-08-08 2018-03-28 Nippon Steel & Sumitomo Metal Corporation Hartstahldraht mit hervorragender drahtziehbarkeit
US10487379B2 (en) 2014-08-08 2019-11-26 Nippon Steel Corporation High-carbon steel wire rod with excellent wire drawability

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JP5092749B2 (ja) 2012-12-05
US20110284139A1 (en) 2011-11-24
KR20080017433A (ko) 2008-02-26
WO2007139234A1 (ja) 2007-12-06
CA2617381A1 (en) 2007-12-06
CN101341270B (zh) 2012-04-18
BRPI0702892B1 (pt) 2014-11-18
US20090087336A1 (en) 2009-04-02
EP2025769A4 (de) 2010-08-18
BRPI0702892A2 (pt) 2011-03-15
CN101341270A (zh) 2009-01-07
CA2617381C (en) 2013-09-17
KR101018054B1 (ko) 2011-03-02
JPWO2007139234A1 (ja) 2009-10-15

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