EP2238271A1 - Tiges de fil métallique pour étirage présentant une résistance et une ductilité élevées, et procédé de fabrication de telles tiges - Google Patents

Tiges de fil métallique pour étirage présentant une résistance et une ductilité élevées, et procédé de fabrication de telles tiges

Info

Publication number
EP2238271A1
EP2238271A1 EP08867709A EP08867709A EP2238271A1 EP 2238271 A1 EP2238271 A1 EP 2238271A1 EP 08867709 A EP08867709 A EP 08867709A EP 08867709 A EP08867709 A EP 08867709A EP 2238271 A1 EP2238271 A1 EP 2238271A1
Authority
EP
European Patent Office
Prior art keywords
wire rod
less
strength
steel
excluding
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Withdrawn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
EP08867709A
Other languages
German (de)
English (en)
Other versions
EP2238271A4 (fr
Inventor
Choong Yeol Lee
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.)
Posco Holdings Inc
Original Assignee
Posco Co Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Posco Co Ltd filed Critical Posco Co Ltd
Publication of EP2238271A1 publication Critical patent/EP2238271A1/fr
Publication of EP2238271A4 publication Critical patent/EP2238271A4/fr
Withdrawn legal-status Critical Current

Links

Classifications

    • 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
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
    • B21C1/003—Drawing materials of special alloys so far as the composition of the alloy requires or permits special drawing methods or sequences
    • 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
    • C22C38/04—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
    • 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 present invention relates to a wire rod for drawing having superior strength and ductility, the wire rod being used for a tire cord, a wire rope, a piano wire, a bridge steel wire and the like, and a method for manufacturing the same, and more particularly, to a wire rod for drawing having high strength and high ductility by controlling a C content to a suitable range and simultaneously adding Si and Cr together to produce a lamella structure of pearlite into a fine pearlite microstructure, and a method for manufacturing the same.
  • the strength of a base steel may be enhanced by adding a large amount of a strengthening element to the base steel.
  • Carbon (C) is a representative example of the strengthening element.
  • the strength of a desired wire rod is increasingly enhanced as the content of C increases from a hypoeutectoid zone to a eutectoid zone, and from a eutectoid zone to a hypereutectoid zone.
  • a wire rod for drawing is prepared by drawing and heat-treating a rolled wire rod and finally processing the rolled wire rod into a wire rod.
  • the rolled wire rod may be cured to drastically improve its strength. Since a lamellar spacing of the pearlite structure becomes fine, a strain-hardening coefficient increases, and a potential is piled up in the process of the wire rod, it is possible to cure the wire rod.
  • strength of a wire rod may be enhanced by increasing a wire drawing strain of material, regardless of the above-mentioned processes.
  • the wire drawing strain of material is closely associated with the ductility of material. Where a material is not dis- connected while being drawn, the steel material may be easily processed and the strength of a wire rod may be favorably improved.
  • the present invention is designed to solve the problems of the prior art, and therefore it is an object of the present invention to provide a wire rod for drawing having high strength and high ductility by controlling a C content to a suitable range and simultaneously adding Si and Cr together to produce a lamella structure of pearlite into a fine pearlite microstructure.
  • a wire rod for drawing which has superior strength and ductility, including, by weight: carbon (C): 0.87 to 1.0%, manganese (Mn): 0.1 to 0.60%, silicon (Si): 0.3 to 1.0%, sulfur (S): 0.010% or less (excluding 0%), phosphorus (P): 0.011% or less (excluding 0%), chromium (Cr): 0.1 to 0.5%, nitrogen (N): 0.007% or less (excluding 0%), and the balance of iron (Fe) and other inevitable impurities, wherein the sum (% by weight) of the Si and Cr contents satisfies the following equation: 0.6 ⁇ Si+Cr ⁇ 1.2, and the wire rod has a pearlite structure.
  • one exemplary embodiment of the present invention may provide a wire rod for drawing, which has high strength and high ductility, by controlling a C content to a suitable range and simultaneously adding Si and Cr together.
  • another exemplary embodiment of the present invention may provide a method for manufacturing a wire rod for drawing having high strength and high ductility.
  • FIG. 1 is a graph illustrating tensile strength and reduction of area of a wire rod for drawing according to the content of carbon (C).
  • FIG. 2 is a graph illustrating tensile strength and reduction of area of a wire rod for drawing according to the compositional ranges of components in the wire rod.
  • FIG. 1 is a graph illustrating tensile strength and reduction of area of a wire rod according to the content of carbon (C). Referring to FIG. 1, when the content of C increase to a level of constant C content, it is difficult to expect improvement of the strength of the wire rod, and the strength of the wire rod is not enhanced, or rather decreased due to the small reduction of area.
  • the strength and ductility of the wire rod for drawing may be secured by adjusting the C content to a content level at which the reduction of area of the wire rod may be secured without the continuous increases in the C content, and simultaneously adding other alloy elements, particularly Si and Cr, to produce a lamella structure of pearlite into a fine pearlite microstructure.
  • compositional ranges of components in the steel sheet according to one exemplary embodiment of the present invention are described in more detail.
  • the term 'percentage (%)' used in the exemplary embodiments represents '% by weight', unless indicated otherwise.
  • Carbon (C) is a core element to secure strength of steel.
  • a content of C exceeds 1.0%, the reduction of area (RA) of the steel is decreased, which makes it impossible to expect the improvement of the strength of steel by a drawing process, whereas, when the content of C is less than 0.87%, it is difficult to secure a desired strength of steel. Therefore, it is desirable to define the C content to 0.87 to 1.0%.
  • Manganese (Mn) is an element that is effective at enhancing hardenability of steel but causes severe center segregation. In this case, when a content of Mn exceeds 0.6%, Mn has high possibility to induce formation of a low-temperature structure. On the contrary, when the content of Mn is less than 0.1%, an addition effect of Mn may not be shown sufficiently. Therefore, it is desirable to define the Mn content to 0.1 to 0.6%.
  • Si silicon
  • C functions to enhance the strength of steel with its increasing content, but results in the decrease in reduction of area of steel, which appears as limits on the improvement of the strength of steel.
  • C functions to precipitate coarse proeutectoid cementite beyond a hypereutectoid compositional range, which provides a main crack initiation position during a drawing process.
  • the addition of Si does not facilitate the formation of proeutectoid cementite within the hypereutectoid compositional range, but functions to enhance the strength of steel by means of the solution strengthening.
  • Si is used as a deoxidizing agent in a steel-making process, a trace of Si is included in steel.
  • Si is added at a content of less than 0.3%, the strength and ductility of steel are not improved effectively.
  • the content of the added Si exceeds 1.0%, the ductility of lamellar ferrite may be deteriorated severely, thereby degrading wire drawability. Therefore, it is desirable to define the Si content to 0.3 to 1.0%.
  • Cr chromium
  • Cr functions to improve the strength and ductility of steel by producing a lamella structure of pearlite into a fine pearlite mi- crostructure.
  • a content of Cr is less than 0.1%, the lamellar structure of pearlite into a fine pearlite microstructure is not achieved sufficiently, whereas, when the content of Cr exceeds 0.5%, a pearlite transformation rate at constant temperature is slow, which adversely affects productivity of steel. Therefore, it is desirable to define the Cr content to 0.1 to 0.5%.
  • S Sulfur
  • P Phosphorus
  • N Nitrogen
  • the wire rod satisfying the requirements regarding the above-mentioned compositional ranges may further include nickel (Ni).
  • Ni functions to improve the strength and ductility of a wire rod since it facilitates the plastic deformation of cementite during a drawing process by driving one more slip system of cementite.
  • Ni When a content of Ni is less than 0.3%, the strength and ductility of a wire rod are not significantly changed when compared to those of the wire rod that does not include Ni but satisfies the requirements regarding the above-mentioned compositional ranges. Therefore, it is desirable for the wire rod to include 0.3% or more of Ni.
  • Ni may be more preferably used at a content of 0.3 to 1.0%.
  • the wire rod for drawing includes the balance of iron (Fe) and other inevitable impurities.
  • the wire rod having the above-mentioned compositional ranges has a tensile strength of 1300 MPa or more and a 30% or more reduction of area.
  • a pearlite structure has an interlamellar spacing of 130 nm or less.
  • the pearlite structure of the wire rod has an interlamellar spacing of 50 nm or less. The finer the interlamellar spacing of the pearlite structure is, the higher the strength of the wire rod is.
  • each of steel billets having components and their contents as listed in the following Table 1 was heated at 1100 to 1300 0 C, and hot-rolled, and then cooled at a rate of 10 to 20 °C/s to obtain a wire rod. Then, each of the prepared wire rods was measured for tensile strength (TS), reduction of area (RA), and interlamellar spacing of a pearlite structure.
  • FIG. 2 is a graph illustrating tensile strength and reduction of area of a wire rod for drawing according to the addition of Cr and Si in addition to 0.92% by weight of C.
  • the rightmost bar graph represents a tensile strength and a reduction of area of the Inventive steel 1.
  • Inventive steel 4 shows its superior strength and ductility, i.e. a tensile strength of 1364 MPa and a 38.7% reduction of area. Also, it was seen that the Inventive steel 4 has a tensile strength of 1300 MP or more and a 30% or more reduction of area when the sum of the Si and Cr contents is in a range of 0.6 to 1.2 % by weight. Also, it was revealed that the Inventive steel 5 shows its superior tensile strength and reduction of area when Ni is added at a content of 0.5 % by weight.
  • Example 2 (Example 2) [93] Each of the wire rods (Inventive steel 1, Comparative steels 4 and 5) prepared in the method of Example 1 was austenized at 1050 0 C, lead-patented at a solder pot temperature of 55O 0 C to obtain a steel sheet. Then, each of the steel sheets was measured for tensile strength and interlamellar spacing. The results are listed in the following Table 2.
  • the twists represent the workability or ductility of a steel wire at maintaining its superior strength.
  • the superior ductility of a wire rod functions to reduce a disconnection rate of the wire rod during the drawing process and suppress the delamination in the wire rod.
  • the fatigue property represents the increase in service life and durability of the wire rod.
  • the fatigue property is two times higher in the Inventive steels than the Comparative steels. Therefore, it was seen that, owing to the combined addition of Si and Cr, the Inventive steel 1 shows its superior ductility and fatigue property as well as the tensile strength even after the drawing process.

Landscapes

  • 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)

Abstract

L'invention concerne une tige de fil métallique pour étirage présentant une résistance et une ductilité élevées, et un procédé de fabrication d'une telle tige. Cette tige de fil métallique pour étirage comprend, en pourcentage en poids: du carbone (C): 0,87 à 1,0%, du manganèse (Mn): 0,1 à 0,60%, du silicium (Si): 0,3 à 1,0%, du soufre (S): 0,010% ou moins (à l'exclusion de 0%), du phosphore (P): 0,011% ou moins (à l'exclusion de 0%), du chrome (Cr): 0,1 à 0,5%, de l'azote (N): 0,007% ou moins (à l'exclusion de 0%), le reste étant du fer (Fe) et d'autres impuretés inévitables, la somme de la teneur en Si et Cr répondant à l'équation: 0,6 ≤ Si+Cr ≤1,2 (la teneur en Si et Cr étant représentée par son en pourcentage en poids), et la tige de fil métallique présentant une structure de perlite.
EP08867709.1A 2007-12-27 2008-11-12 Tiges de fil métallique pour étirage présentant une résistance et une ductilité élevées, et procédé de fabrication de telles tiges Withdrawn EP2238271A4 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR1020070139434A KR100979006B1 (ko) 2007-12-27 2007-12-27 강도와 연성이 우수한 신선용 선재 및 그 제조방법
PCT/KR2008/006660 WO2009084811A1 (fr) 2007-12-27 2008-11-12 Tiges de fil métallique pour étirage présentant une résistance et une ductilité élevées, et procédé de fabrication de telles tiges

Publications (2)

Publication Number Publication Date
EP2238271A1 true EP2238271A1 (fr) 2010-10-13
EP2238271A4 EP2238271A4 (fr) 2014-10-01

Family

ID=40824498

Family Applications (1)

Application Number Title Priority Date Filing Date
EP08867709.1A Withdrawn EP2238271A4 (fr) 2007-12-27 2008-11-12 Tiges de fil métallique pour étirage présentant une résistance et une ductilité élevées, et procédé de fabrication de telles tiges

Country Status (6)

Country Link
US (1) US20100263772A1 (fr)
EP (1) EP2238271A4 (fr)
JP (1) JP2011509345A (fr)
KR (1) KR100979006B1 (fr)
CN (1) CN101910440A (fr)
WO (1) WO2009084811A1 (fr)

Families Citing this family (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008069409A (ja) * 2006-09-14 2008-03-27 Bridgestone Corp 高強度高炭素鋼線およびその製造方法
KR101309881B1 (ko) * 2009-11-03 2013-09-17 주식회사 포스코 신선가공성이 우수한 신선용 선재, 초고강도 강선 및 그 제조방법
EP2557191B1 (fr) * 2010-04-08 2016-07-27 Nippon Steel & Sumitomo Metal Corporation Matériau de fil pour fil de scie et procédé de fabrication de ce dernier
US8707944B2 (en) 2010-06-15 2014-04-29 Nippon Steel & Sumitomo Metal Corporation Saw wire
JP5411820B2 (ja) * 2010-09-06 2014-02-12 株式会社神戸製鋼所 フラックス入り溶接ワイヤ及びこれを用いた肉盛溶接のアーク溶接方法
US20120128524A1 (en) * 2010-11-22 2012-05-24 Chun Young Soo Steel wire rod having excellent cold heading quality and hydrogen delayed fracture resistance, method of manufacturing the same, and mehod of manufacturing bolt using the same
KR101271956B1 (ko) * 2011-06-28 2013-06-07 주식회사 포스코 우수한 피로강도를 갖는 고강도 선재 및 그 제조방법
KR101353649B1 (ko) * 2011-12-23 2014-01-20 주식회사 포스코 내부식성이 우수한 스프링용 선재 및 강선, 스프링용 강선 및 스프링의 제조방법
KR101428174B1 (ko) 2012-07-13 2014-08-07 주식회사 포스코 비틀림 특성이 우수한 강선 및 그 제조방법
KR101518602B1 (ko) * 2013-10-29 2015-05-07 주식회사 포스코 비틀림 특성이 우수한 고강도 강선의 제조방법
US10329646B2 (en) 2014-08-15 2019-06-25 Nippon Steel & Sumitomo Metal Corporation Steel wire for drawing
JP6416709B2 (ja) * 2015-07-21 2018-10-31 新日鐵住金株式会社 高強度ｐｃ鋼線
KR101696095B1 (ko) 2015-08-28 2017-01-13 주식회사 포스코 신선성이 우수한 열처리재의 제조방법
JP6481770B2 (ja) * 2015-10-23 2019-03-13 新日鐵住金株式会社 伸線加工用鋼線材
KR101758477B1 (ko) * 2015-12-11 2017-07-27 주식회사 포스코 강도 및 내식성이 우수한 고탄소강 선재, 강선 및 이들의 제조방법
CN105568134A (zh) * 2016-01-05 2016-05-11 江阴兴澄特种钢铁有限公司 一种微合金化轿车碳素轮毂轴承用钢及其制造方法
JP6762131B2 (ja) * 2016-04-28 2020-09-30 株式会社神戸製鋼所 フラックス入りワイヤ
JP6922726B2 (ja) * 2017-12-26 2021-08-18 日本製鉄株式会社 熱間圧延線材
CN112840044B (zh) * 2018-10-16 2022-11-22 日本制铁株式会社 热轧线材

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5240520A (en) * 1990-11-19 1993-08-31 Nippon Steel Corporation High strength, ultra fine steel wire having excellent workability in stranding and process and apparatus for producing the same
JP2001220649A (ja) * 2000-02-08 2001-08-14 Nippon Steel Corp 延性及び疲労特性の優れた高強度極細鋼線
JP2004091912A (ja) * 2002-09-04 2004-03-25 Sumitomo Metal Ind Ltd 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
US20040118486A1 (en) * 2002-12-18 2004-06-24 Zelin Michael Gregory High strength, high carbon steel wire

Family Cites Families (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2735647B2 (ja) * 1988-12-28 1998-04-02 新日本製鐵株式会社 高強度高延性鋼線材および高強度高延性極細鋼線の製造方法
JP3221943B2 (ja) * 1992-11-24 2001-10-22 新日本製鐵株式会社 伸線加工性の良好な高強度極細線用低合金鋼線材およびその製造方法
JP3283332B2 (ja) * 1993-04-08 2002-05-20 新日本製鐵株式会社 撚り線加工性の優れた高強度極細鋼線およびその製造方法
KR0143499B1 (ko) * 1994-12-21 1998-08-17 김만제 연성이 우수한 초고장력 과공석 탄소강 선재의 제조방법
KR100256334B1 (ko) * 1995-12-26 2000-05-15 이구택 신선성이 우수한 고강도 선재 제조방법
JPH11315349A (ja) * 1998-04-30 1999-11-16 Kobe Steel Ltd 耐遅れ破壊性に優れた高強度線材およびその製造方法並びに高強度ボルト
JP3940270B2 (ja) * 2000-04-07 2007-07-04 本田技研工業株式会社 耐遅れ破壊性および耐リラクセーション特性に優れた高強度ボルトの製造方法
JP4003450B2 (ja) * 2001-12-13 2007-11-07 住友金属工業株式会社 鋼線材、鋼線及びその製造方法
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
JP4016894B2 (ja) * 2003-06-12 2007-12-05 住友金属工業株式会社 鋼線材及び鋼線の製造方法
JP4374357B2 (ja) * 2005-06-29 2009-12-02 新日本製鐵株式会社 伸線特性に優れた高強度線材及びその製造方法、並びに伸線特性に優れた高強度鋼線
JP4593504B2 (ja) * 2006-03-28 2010-12-08 新日本製鐵株式会社 延性に優れた高強度極細鋼線

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5240520A (en) * 1990-11-19 1993-08-31 Nippon Steel Corporation High strength, ultra fine steel wire having excellent workability in stranding and process and apparatus for producing the same
JP2001220649A (ja) * 2000-02-08 2001-08-14 Nippon Steel Corp 延性及び疲労特性の優れた高強度極細鋼線
JP2004091912A (ja) * 2002-09-04 2004-03-25 Sumitomo Metal Ind Ltd 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
US20040118486A1 (en) * 2002-12-18 2004-06-24 Zelin Michael Gregory High strength, high carbon steel wire

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of WO2009084811A1 *

Also Published As

Publication number Publication date
KR20090071206A (ko) 2009-07-01
WO2009084811A1 (fr) 2009-07-09
CN101910440A (zh) 2010-12-08
JP2011509345A (ja) 2011-03-24
KR100979006B1 (ko) 2010-08-30
EP2238271A4 (fr) 2014-10-01
US20100263772A1 (en) 2010-10-21

Similar Documents

Publication Publication Date Title
US20100263772A1 (en) Wire rods having superior strength and ductility for drawing and method for manufacturing the same
JP5233281B2 (ja) 延性に優れた高強度鋼線およびその製造方法
JP5162875B2 (ja) 伸線特性に優れた高強度線材およびその製造方法
JP5088631B2 (ja) 疲労特性と曲げ成形性に優れた機械構造鋼管とその製造方法
JP2016534230A (ja) 高硬度熱間圧延鋼材製品及びその製造方法
JP5761080B2 (ja) 伸びと穴拡げ性と疲労特性に優れた高強度熱延鋼板及びその製造方法
WO2008102573A1 (fr) Fil d'acier à ressort haute résistance, ressorts haute résistance et procédé de fabrication des deux
KR101344537B1 (ko) 고강도 강판 및 그 제조 방법
JP2007131945A (ja) 延性に優れた高強度鋼線およびその製造方法
JP3536684B2 (ja) 伸線加工性に優れた鋼線材
CN111542637B (zh) 高强度奥氏体基高锰钢材及其制造方法
CN113966404A (zh) 具有优异的可拉拔性和冲击韧性的非热处理线材及其制造方法
CN108220547B (zh) 高强度低屈服比型微细球化钢板及其制造方法
KR101412247B1 (ko) 초고강도 강판 제조 방법
KR100431849B1 (ko) 저온조직이 없는 고실리콘 첨가 중탄소강 선재의 제조방법
JP2023508314A (ja) 超高強度ばね用線材、鋼線及びその製造方法
KR101443445B1 (ko) 비열처리형 고강도 열연강판 및 그 제조 방법
KR101518583B1 (ko) 신선가공성이 우수한 고강도 선재, 강선 및 이들의 제조방법
JP5896673B2 (ja) せん断加工部品用熱延鋼板およびせん断加工部品用鋼板の製造法
KR100431848B1 (ko) 저온조직이 없는 고실리콘 첨가 고탄소 선재의 제조방법
JP7472826B2 (ja) 電縫溶接鋼管およびその製造方法
JPH1177116A (ja) 高疲労強度鋼管の製造方法
KR101443446B1 (ko) 비열처리형 열연강판 및 그 제조 방법
KR20240022723A (ko) 고강도 및 고연신 강판
KR101505302B1 (ko) 고강도 강판 및 그 제조 방법

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20100722

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MT NL NO PL PT RO SE SI SK TR

AX Request for extension of the european patent

Extension state: AL BA MK RS

DAX Request for extension of the european patent (deleted)
A4 Supplementary search report drawn up and despatched

Effective date: 20140903

RIC1 Information provided on ipc code assigned before grant

Ipc: C21D 8/00 20060101ALI20140828BHEP

Ipc: C22C 38/18 20060101ALI20140828BHEP

Ipc: C22C 38/04 20060101ALI20140828BHEP

Ipc: C22C 38/08 20060101ALI20140828BHEP

Ipc: C22C 38/02 20060101ALI20140828BHEP

Ipc: C22C 38/00 20060101AFI20140828BHEP

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE APPLICATION IS DEEMED TO BE WITHDRAWN

18D Application deemed to be withdrawn

Effective date: 20150331