EP3336205B1 - Hochfester stahldraht und verfahren zur herstellung desselben - Google Patents

Hochfester stahldraht und verfahren zur herstellung desselben Download PDF

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Publication number
EP3336205B1
EP3336205B1 EP17207431.2A EP17207431A EP3336205B1 EP 3336205 B1 EP3336205 B1 EP 3336205B1 EP 17207431 A EP17207431 A EP 17207431A EP 3336205 B1 EP3336205 B1 EP 3336205B1
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EP
European Patent Office
Prior art keywords
steel wire
steel
strength
pearlite
cementite
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.)
Active
Application number
EP17207431.2A
Other languages
English (en)
French (fr)
Other versions
EP3336205A1 (de
Inventor
Choong Yeol Lee
Yong Sik Park
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 EP3336205A1 publication Critical patent/EP3336205A1/de
Application granted granted Critical
Publication of EP3336205B1 publication Critical patent/EP3336205B1/de
Active legal-status Critical Current
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Classifications

    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • 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
    • 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
    • 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
    • C21D2211/003—Cementite
    • 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 disclosure relates to a high-strength steel wire and a method of manufacturing the high-strength steel wire.
  • Pearlite steel wires produced through a cold drawing process have good mechanical characteristics with an appropriate degree of ductility in combination therewith, and are widely used as one of the highest-strength steel materials known, in applications such as tire cords and bridge cables.
  • KR 2016 0075956 A relates to a high strength steel wire and a manufacturing method thereof . More specifically, the steel wire comprises: carbon (C), manganese (Mn), silicon (Si), nickel (Ni), iron (Fe) and unavoidable impurities.
  • the high strength steel wire has 17% at. % or less of carbon content in a pearlite phase of the steel wire.
  • JP 2004 360005 A relates to a steel wire with delayed fracture properties, having a composition comprising by weight, 0.6-1.2% C, 0.12-2% Si, 0.3-1.0% Mn, ⁇ 0.025% P and ⁇ 0.0025% S, and if required, further comprising one of Al, Cr, Mo, Ni, Cu, V, Nb, W, Ti and B, the balance being iron and unavoidable impurities.
  • aspects of the present disclosure provide a high-strength steel wire configured to have markedly increased tensile strength after a drawing process, and a method of manufacturing the high-strength steel wire.
  • a high-strength steel wire includes, by wt%, carbon (C): 0.52% to 0.72%, manganese (Mn): 0.6% to 0.8%, silicon (Si): 0.1% to 0.4%, nickel (Ni): 0.3% to 1.2%, vanadium (V): 0.3% to 1.2%, and a balance of iron (Fe) and inevitable impurities, wherein after a drawing process, the high-strength steel wire has a carbon content of 20 at.% or less in cementite within pearlite,
  • a method of manufacturing a high-strength steel wire as defined in the foregoing includes: heating a steel billet satisfying the above-described alloying composition; finish hot rolling the heated steel billet at a temperature of 900°C to 1200°C to manufacture a wire rod; cooling the wire rod to room temperature at a cooling rate of 5°C/s to 20°C/s; and drawing the cooled wire rod to manufacture a steel wire, wherein the steel wire has a carbon content of 20 at.% or less in cementite within pearlite and wherein the drawing is performed at a strain ( ⁇ ) of 60% to 90%.
  • nickel (Ni) and vanadium (V) are added to steel according to the present disclosure as alloying elements, and since nickel (Ni) and vanadium (V) facilitate the decomposition of cementite, the amount of carbon (C) moving into ferrite increases, even with the same amount of drawing, thereby proving a high-strength steel wire.
  • a high-strength steel wire includes, by wt%, carbon (C) : 0.52% to 0.72%, manganese (Mn): 0.6% to 0.8%, silicon (Si): 0.1% to 0.4%, nickel (Ni): 0.3% to 1.2%, and vanadium (V): 0.3% to 1.2%.
  • Carbon (C) is a key element guaranteeing strength. However, if the content of carbon (C) in steel is excessively high, the area reduction ratio of a steel material may be decreased, and thus, a strength improving effect may not be obtained through a drawing process. In addition, if the content of carbon (C) is excessively low, a desired degree of strength may not be obtained.
  • the content of carbon (C) it is necessary to adjust the content of carbon (C) to be within the range of 0.52% to 0.72%. More preferably, the content of carbon (C) may be adjusted to be within the range of 0.55% to 0.70%.
  • Manganese (Mn) excessively segregates along a centreline. If the content of manganese (Mn) is greater than 0.8%, a low-temperature microstructure may very likely be formed, and thus it is necessary that the content of manganese (Mn) is adjusted to be 0.8% or less. However, if the content of manganese (Mn) is excessively low, less than 0.6%, it is difficult to guarantee hardenability.
  • the content of manganese (Mn) it is necessary to adjust the content of manganese (Mn) to be within the range of 0.6% to 0.8%. More preferably, the content of manganese (Mn) may be adjusted to be within the range of 0.65% to 0.75%.
  • Silicon (Si) is effective in improving strength because silicon (Si) preferentially dissolves in ferrite. To this end, it is necessary that silicon (Si) is added in an amount of 0.1% or greater. However, if the content of silicon (Si) is excessively high, greater than 0.4%, the ductility of steel may be reduced.
  • the content of silicon (Si) it is necessary to adjust the content of silicon (Si) to be within the range of 0.1% to 0.4%. More preferably, the content of silicon (Si) may be adjusted to be within the range of 0.15% to 0.30%.
  • Nickel (Ni) has a function of facilitating the decomposition of cementite by causing interfaces of pearlite lamellae to become unstable, and a function of improving plastic deformability by increasing the number of operable slip systems of cementite in pearlite.
  • Ni nickel (Ni) is 0.3% or greater.
  • nickel (Ni) is a relatively expensive element, when production costs are considered, it is necessary that the content of nickel (Ni) is adjusted to be 1.2% or less.
  • the content of nickel (Ni) it is necessary to adjust the content of nickel (Ni) to be within the range of 0.3% to 1.2%. More preferably, the content of nickel (Ni) may be adjusted to be within the range of 0.5% to 1.0%.
  • Vanadium (V) is an element precipitating in steel in the form of vanadium carbide (VC) and thus improving strength.
  • VC vanadium carbide
  • Ni nickel
  • vanadium (V) causes interfaces of pearlite lamellae to become unstable, thereby facilitating the decomposition of cementite.
  • vanadium in an amount of 0.3% or greater.
  • ductility may sharply decrease due to clumping of precipitate particles, and thus drawability may deteriorate.
  • the content of vanadium (V) it is necessary to adjust the content of vanadium (V) to be within the range of 0.3% to 1.2%. More preferably, the content of vanadium (V) may be adjusted to be within the range of 0.4% to 1.0%.
  • the other component of the high-strength steel wire of the present disclosure is iron (Fe).
  • Fe iron
  • impurities of raw materials or in manufacturing environments may be inevitably included in the high-strength steel wire , and such impurities may not be removed from the high-strength steel wire.
  • Such impurities are well-known to those of ordinary skill in manufacturing industries, and thus specific descriptions of the impurities will not be given in the present disclosure.
  • the carbon content of cementite included in pearlite is 20 at.% or less.
  • cementite consists of three iron (Fe)atoms and one carbon (C) atom
  • the carbon content of cementite (Fe 3 C) included in pearlite is 25 at. % before a drawing process.
  • the carbon content of cementite included in pearlite decreases below 25 at.%, and this means that cementite included in pearlite is plastically deformed and also decomposed by the drawing process .
  • This decomposition of cementite occurs because a stable energy state is achieved when carbon separates from cementite and moves into a ferrite matrix.
  • the steel wire of the present disclosure has a tensile strength of 1450 MPa or greater and an elongation of 13% or greater.
  • the steel wire of the present disclosure has a pearlite lamellar spacing of 180 nm or less. If the pearlite lamellar spacing is greater than 180 nm, the strength and ductility of the steel wire decrease as the pearlite lamellar spacing increases. Since the steel wire is required to have a smaller pearlite lamellar spacing, the lower limit of the pearlite lamellar spacing is not specifically set.
  • a steel wire is manufactured by manufacturing a wire rod having the above-described alloying composition and performing a drawing process on the wire rod.
  • the wire rod may be manufactured using various rod manufacturing methods generally known in the art. However, the wire rod may be manufactured through a series of processes to be described below.
  • a steel billet having the above-described alloying composition is manufactured, and the steel billet is heated to within austenite temperature range. Then, a hot rolling process is performed on the steel billet to form a wire rod.
  • finish hot rolling it is necessary that finish hot rolling be performed at a temperature of 900°C to 1200°C. If the temperature of finish hot rolling is lower than 900°C, the lifespan of rolls may decrease due to a large rolling load. Conversely, if the temperature of finish hot rolling is higher than 1200°C, the size of grains may increase to cause a decrease in ductility, and decarbonization may occur excessively, leading to a deterioration in drawability.
  • the wire rod After the finish hot rolling, it is necessary that the wire rod be cooled to room temperature at a cooling rate of 5°C/s to 20°C/s.
  • wire rod is cooled at a cooling rate lower than 5°C/s, drawability may deteriorate because of the formation of pro-eutectoid ferrite, and if the wire rod is cooled at a cooling rate higher than 20°C/s, a low-temperature microstructure may be formed.
  • a steel wire is manufactured by performing a drawing process on the cooled wire rod at a strain ( ⁇ ) of 60% to 90%.
  • the strain is less than 60%, it may be difficult to obtain a sufficient degree of strength, and if the strain is greater than 90%, delamination may occur and thus, the possibility of product defects may increase.
  • the steel wire of the present disclosure obtained through the drawing process has a carbon content of 20 at.% or less in cementite within pearlite, a tensile strength of 1450 MPa or greater, and an elongation of 13% or greater.
  • Inventive Steel 1 further included 0.6 wt% nickel (Ni) and 0.5 wt% vanadium (V) when compared to Comparative Steel 1, and after the drawing process, the content of carbon in cementite of Inventive Steel 1 decreased to 19 at.%.
  • Inventive Steel 2 further including 1.0 wt% nickel (Ni) and 1.0 wt% vanadium (V), as compared to Comparative Steel 1, had a carbon content of 17 at. % in cementite within pearlite which was much lower than that of Comparative Steel 1. Owing to this, Inventive Steel 2 had a tensile strength of 1532 MPa and an elongation of 14.2% which were much higher than those of Comparative Steel 1.
  • nickel (Ni) and vanadium (V) are added together in appropriate amounts, and thus, lamellar spacing is decreased. This affects the strength and ductility of steel.
  • nickel (Ni) and vanadium (V) are added as alloying elements to effectively facilitate the decomposition of cementite in pearlite after a drawing process, thereby providing a high-strength steel wire having improved tensile strength.

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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)

Claims (2)

  1. Hochfester Stahldraht, umfassend in Gew.-% Kohlenstoff (C): 0,52 % bis 0,72 %, Mangan (Mn): 0,6 % bis 0,8 %, Silizium (Si): 0,1 % bis 0,4 %, Nickel (Ni): 0,3 % bis 1,2 %, Vanadium (V): 0,3 % bis 1,2 % und einen Rest an Eisen (Fe) und unvermeidlichen Verunreinigungen,
    wobei der hochfeste Stahldraht nach einem Ziehvorgang einen Kohlenstoffgehalt von 20 Atom- % oder weniger in Zementit innerhalb von Perlit aufweist,
    wobei der hochfeste Stahldraht einen Perlit-Lamellenabstand von 180 nm oder weniger aufweist, und
    wobei der hochfeste Stahldraht eine Zugfestigkeit von 1450 MPa oder mehr und eine Dehnung von 13 % oder mehr aufweist.
  2. Verfahren zum Herstellen eines hochfesten Stahldrahts nach Anspruch 1, wobei das Verfahren umfasst:
    Erhitzen eines Stahlknuppels, umfassend in Gew.-% Kohlenstoff (C): 0,52 % bis 0,72 %, Mangan (Mn): 0,6 % bis 0,8 %, Silizium (Si): 0,1 % bis 0,4 %, Nickel (Ni): 0,3 % bis 1,2 %, Vanadium (V): 0,3 % bis 1,2 % und einen Rest an Eisen (Fe) und unvermeidlichen Verunreinigungen;
    Beenden des Warmwalzens des erhitzten Stahllknuppels bei einer Temperatur von 900 °C bis 1200 °C, um einen Walzdraht herzustellen;
    Abkühlen des Walzdrahts auf Raumtemperatur mit einer Abkühlgeschwindigkeit von 5 °C/s bis 20 °C/s; und
    Ziehen des abgekühlten Walzdrahts zur Herstellung eines Stahldrahts,
    wobei der Stahldraht einen Kohlenstoffgehalt von 20 Atom-% oder weniger in Zementit innerhalb von Perlit aufweist, und
    wobei das Ziehen bei einer Dehnung (ε) von 60 % bis 90 % durchgeführt wird.
EP17207431.2A 2016-12-16 2017-12-14 Hochfester stahldraht und verfahren zur herstellung desselben Active EP3336205B1 (de)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
KR1020160172657A KR101889179B1 (ko) 2016-12-16 2016-12-16 고강도 강선 및 이의 제조방법

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EP3336205A1 EP3336205A1 (de) 2018-06-20
EP3336205B1 true EP3336205B1 (de) 2020-06-03

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP4265768A4 (de) * 2020-12-15 2024-11-27 POSCO Co., Ltd Stahldraht mit verbesserter ziehbarkeit und herstellungsverfahren dafür

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2974546B2 (ja) * 1993-06-04 1999-11-10 新日本製鐵株式会社 疲労特性に優れた極細鋼線
JP3499341B2 (ja) * 1995-05-29 2004-02-23 株式会社神戸製鋼所 ゴム補強用鋼線の製造方法
JP3840376B2 (ja) 2000-12-20 2006-11-01 株式会社神戸製鋼所 疲労強度および延性に優れた硬引き線用鋼材および硬引き伸線材
JP4146205B2 (ja) * 2002-10-10 2008-09-10 新日本製鐵株式会社 耐遅れ破壊特性の良好なｐｃ鋼線およびその製造方法ならびにｐｃ撚り線
JP4319840B2 (ja) * 2003-01-27 2009-08-26 新日本製鐵株式会社 高強度、高靭性高炭素鋼線材とその製造方法
JP4267376B2 (ja) * 2003-06-04 2009-05-27 新日本製鐵株式会社 遅れ破壊特性の優れた高強度ｐｃ鋼線およびその製造方法
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
KR20160075956A (ko) * 2014-12-19 2016-06-30 주식회사 포스코 고강도 강선 및 이의 제조방법

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP4265768A4 (de) * 2020-12-15 2024-11-27 POSCO Co., Ltd Stahldraht mit verbesserter ziehbarkeit und herstellungsverfahren dafür

Also Published As

Publication number Publication date
KR20180070214A (ko) 2018-06-26
EP3336205A1 (de) 2018-06-20
KR101889179B1 (ko) 2018-08-16

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