US20160097113A1 - High-strength spring steel having excellent wire-rod rolling properties - Google Patents

High-strength spring steel having excellent wire-rod rolling properties Download PDF

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US20160097113A1
US20160097113A1 US14/874,671 US201514874671A US2016097113A1 US 20160097113 A1 US20160097113 A1 US 20160097113A1 US 201514874671 A US201514874671 A US 201514874671A US 2016097113 A1 US2016097113 A1 US 2016097113A1
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spring steel
rod rolling
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Kosuke Kimura
Ryosuke OHASHI
Ryohei Ishikura
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Daido Steel Co Ltd
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Daido Steel Co Ltd
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Assigned to DAIDO STEEL CO., LTD. reassignment DAIDO STEEL CO., LTD. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: ISHIKURA, RYOHEI, KIMURA, KOSUKE, OHASHI, Ryosuke
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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
    • 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
    • C22C38/04—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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B60—VEHICLES IN GENERAL
    • B60G—VEHICLE SUSPENSION ARRANGEMENTS
    • B60G2206/00—Indexing codes related to the manufacturing of suspensions: constructional features, the materials used, procedures or tools
    • B60G2206/01—Constructional features of suspension elements, e.g. arms, dampers, springs
    • B60G2206/40—Constructional features of dampers and/or springs
    • B60G2206/42—Springs
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron

Definitions

  • the present invention relates to a high-strength spring steel having excellent wire-rod rolling properties.
  • Patent document 1 has disclosed the technique of heating a steel material at a temperature of 1,170° C. or more for at least 2 minutes under hot rolling, cooling the material at an average cooling rate of 5 to 300° C./min in a temperature range from 750° C. to 600° C. after the rolling, and further adopting descaling process.
  • Patent Document 2 has disclosed the technique of subjecting a steel material to hot rolling in a condition that, after heating furnace extraction, the temperature before finishing is set to less than 1,000° C., keeping the steel material in a temperature range of 1,000° C. to 1,150° C. for 5 seconds or less after finish rolling and then winding it up, thereafter cooling the wound steel material to a temperature of 750° C. or less at a cooling rate of 2 to 8° C./sec, and further gradually cooling down to 600° C. by spending 150 seconds or more after the winding-up.
  • Patent Document 1 Japanese Patent No. 4031267
  • Patent Document 2 Japanese Patent No. 5330181
  • Patent Documents 1 and 2 require execution of individually specified rolling process. Accordingly, it has been desired to avoid occurrence of ferrite decarburization and formation of bainite by adjusting chemical components of a steel material instead of adopting a technique of providing a specific rolling process, thereby developing a high-strength spring steel having excellent wire-rod rolling properties.
  • the present invention has been made against a background of the foregoing circumstances, and an object of the present invention is to provide a high-strength spring steel having excellent wire-rod rolling properties by adjusting chemical components of a steel material to avoid occurrence of ferrite decarburization and formation of bainite.
  • the present invention relates to the following items 1 to 3.
  • a high-strength spring steel having excellent wire-rod rolling properties consisting essentially of, in terms of mass %:
  • the present inventors have found that it is possible to formulate (as Expression (1)) the relation between a ferrite decarburization depth and a parameter (X1) determined by converting the degrees of contributions to the depth from respective chemical components of a steel material into numerical values, formulate (as Expression (2)) the relation between bainite formation in the case of cooling at a normal cooling rate after wire-rod rolling and a parameter (X2) determined by converting the degrees of contributions to the bainite formation from respective chemical components of a steel material into numerical values and formulate (as Expression (3)) the relation between hardness in the case of subjecting tempering treatment at 400° C. and a parameter (X3) determined by converting the degrees of contributions to the hardness from respective chemical components of a steel material into numerical values. Namely, it is possible to obtain a high-strength spring steel having excellent wire-rod rolling properties by adjusting contents of chemical components in a steel material so as to satisfy the foregoing Expressions (1) to (3).
  • FIG. 1 is a graph for illustrating conditions of Expression (1).
  • FIG. 2 is a graph for illustrating conditions of Expression (2).
  • FIG. 3 is a graph for illustrating conditions of Expression (3).
  • FIG. 4 is a graph for showing the reason for setting the lower limit of Ti content to 0.060 mass %.
  • C is an element essential for spring steel to secure strength.
  • the C content is preferably from 0.45% to 0.60%.
  • Si is an element effective in enhancing settling resistance of spring steel. Si is therefore added in an amount of 1.20% or more. However, addition of Si in excess of 2.80% tends to cause not only degradation of settling properties but also occurrence of ferrite decarburization, and hence the upper limit of Si content is set to 2.80%.
  • the Si content is preferably more than 1.50% and 2.50% or less, more preferably more than 2.00% and 2.50% or less.
  • Mn functions as an ingredient for fixing S, which is a tenacity degrading element, in the form of MnS.
  • Mn functions also as a quenching property improver.
  • Mn is added in an amount of 0.30% or more.
  • addition of Mn in an amount exceeding 1.20% results in degradation of tenacity, and hence the upper limit of Mn content is set to 1.20%.
  • the Mn content is preferably more than 0.50% and 1.10% or less, more preferably less than 1.00%.
  • Cu is an element effective in improving corrosion resistance. In addition, it is also effective in preventing ferrite decarburization.
  • the Cu content is preferably from 0.20% to 0.37%.
  • Ni is an element effective in improving corrosion resistance. In addition, it is also effective in preventing ferrite decarburization. Incorporation of Ni, however, brings about an increase in cost, and hence the upper limit of Ni content is set to 0.80%.
  • the Ni content is preferably from 0.50% to 0.75%.
  • Cr is an element effective in improving corrosion resistance. In addition, it is also effective for adjustment of quenching properties. Excessive addition of Cr causes formation of sharp corrosion pits, and hence the upper limit of Cr content is set to 0.70%.
  • the Cr content is preferably from 0.20% to 0.50%.
  • Ti is an element that is apt to form carbide.
  • Ti-based carbides contribute to fining of crystal grains and enhance a fatigue characteristic, a delayed fracture characteristic and settling resistance. For these reasons, Ti is added in an amount of 0.060% or more. When the Ti content exceeds 0.140%, however, the effects of Ti addition become saturated; on the contrary, deterioration in rolling properties is brought about.
  • the upper limit of Ti content is therefore set to 0.140%.
  • the Ti content is preferably from 0.080% to 0.120%. Reasons why the lower limit of Ti content is set to 0.060% will be described later.
  • Al is an element that acts as a deoxidizer during liquid steel treatment. However, when Al is added in an amount exceeding 0.10%, inclusions are increased, whereby lowering of fatigue strength is rather caused.
  • the upper limit of Al content is therefore set to 0.10%.
  • N combines with Ti to form nitride, resulting in lowering of fatigue strength.
  • the upper limit of N content is therefore set to 0.010%.
  • the content thereof is set to 0.0015% or less.
  • FIG. 1 is a graph made by plotting the coordinate data from every steel species with ferrite decarburization depth as vertical axis and X1 in Expression (1) as horizontal axis.
  • X1 includes a polynomial formed by performing addition or subtraction of component terms each of which is obtained by multiplying each of the contents of the specified chemical components (Si, Mn, Cu, Ni and Cr) by the individually specified coefficient and, as clearly seen from FIG. 1 , makes an almost linear correspondence relation with the ferrite decarburization depth.
  • each steel species was melt-formed, and subjected to slabbing and further to wire-rod rolling (13.5 mm ⁇ ) using a real machine at a rolling temperature of 900° C.
  • the cooling rate in this case was set to 0.5° C./sec.
  • an assessment of an actual result of ferrite decarburization in each wire-rod rolled material namely a decision as to whether ferrite decarburization occurred (ferrite decarburization was present) or not (ferrite decarburization was absent), was made.
  • the assessment results are shown in FIG. 1 in the form of coordinate data on every steel species with absence of ferrite decarburization as a white circle and presence of ferrite decarburization as a black circle. Additionally, in Table 1, absence of ferrite decarburization is described as “absent”, while presence of ferrite decarburization is described as “present”.
  • FIG. 2 is a graph made by plotting the coordinate data from every steel species with cooling rate as vertical axis and X2 in Expression (2) as horizontal axis.
  • X2 includes ⁇ and ⁇ as variables, the concept of the equality itself is known (for example, see Materia, vol. 36, No. 6, 1997, pp. 603-608).
  • ⁇ includes a polynomial formed by performing addition or subtraction of component terms each of which is obtained by multiplying each of the contents of the specified chemical components (C, Si, Mn, Cu, Ni and Cr) by the individually specified coefficient, and ⁇ is 10 to the power of such a polynomial. As shown in FIG.
  • FIG. 3 is a graph made by plotting the coordinate data from every steel species with hardness as vertical axis and X3 in Expression (3) as horizontal axis.
  • X3 includes a polynomial formed by performing addition or subtraction of component terms each of which is obtained by multiplying each of the contents of the specified chemical components (C, Si, Mn, Cu, Ni, Cr and Ti) by the individually specified coefficient.
  • the B is an element effective in improving a tenacity of spring steel by preventing P and S from segregating to crystal grain boundaries. Therefore, the B content is preferably 0.0005% or more. On the other hand, excessive addition of B causes formation of nitride of B, thereby resulting in degradation of the tenacity. Therefore, the B content is preferably 0.0050% or less.
  • FIG. 4 is a graph made by plotting the coordinate data from every steel species with crystal grain size number as vertical axis and Ti content as horizontal axis.
  • the austenitic crystal grain size influences various characteristics (a fatigue characteristic, a delayed fracture characteristic, a settling property), and it is generally possible to improve these characteristics through the fining of crystal grains.
  • the lower limit of Ti content is set to 0.060 based on FIG. 4 so that the crystal grain size after quenching-and-tempering becomes No. 9 or more. In other words, by adjusting the Ti content to 0.060% or more, it becomes possible to obtain fine structure which is No. 9 or more in crystal grain size number.
  • the present invention it is possible to obtain a high-strength spring steel having excellent wire-rod rolling properties.
  • the present invention should not be construed as being limited to the foregoing Examples, but can be carried out in modes undergone various changes and modification so long as they do not depart from the gist of the invention.

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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)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
US14/874,671 2014-10-07 2015-10-05 High-strength spring steel having excellent wire-rod rolling properties Abandoned US20160097113A1 (en)

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JP2014206311A JP6458927B2 (ja) 2014-10-07 2014-10-07 線材圧延性に優れた高強度ばね鋼
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JP (1) JP6458927B2 (zh)
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CN106756506A (zh) * 2016-12-30 2017-05-31 天津大强钢铁有限公司 农用挠地旋耕刀合金弹簧钢材料
WO2018230717A1 (ja) * 2017-06-15 2018-12-20 新日鐵住金株式会社 ばね鋼用圧延線材
CN113528981B (zh) * 2021-06-18 2022-04-19 首钢集团有限公司 一种2000MPa级防护用钢板及其制备方法

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US6277220B1 (en) * 1998-06-23 2001-08-21 Takanari Hamada Steel wire rod and process for producing steel for steel wire rod
EP2017358A2 (en) * 2007-07-20 2009-01-21 Kabushiki Kaisha Kobe Seiko Sho Steel wire material for spring and its producing method
US20090065105A1 (en) * 2007-09-10 2009-03-12 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd) Spring steel wire rod excellent in decarburization resistance and wire drawing workability and method for producing same
US20100034691A1 (en) * 2006-10-31 2010-02-11 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Spring steel wire excellent in fatigue characteristic and wire drawability

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JP4588030B2 (ja) * 2004-08-26 2010-11-24 大同特殊鋼株式会社 高強度ばね用鋼、並びに高強度ばね及びその製造方法
JP4423253B2 (ja) * 2005-11-02 2010-03-03 株式会社神戸製鋼所 耐水素脆化特性に優れたばね用鋼、並びに該鋼から得られる鋼線及びばね
WO2008044859A1 (en) * 2006-10-11 2008-04-17 Posco Steel wire rod for high strength and high toughness spring having excellent cold workability, method for producing the same and method for producing spring by using the same
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
KR20140117505A (ko) * 2012-02-14 2014-10-07 제이에프이 스틸 가부시키가이샤 스프링 강
JP5364859B1 (ja) * 2012-05-31 2013-12-11 株式会社神戸製鋼所 コイリング性と耐水素脆性に優れた高強度ばね用鋼線およびその製造方法
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US6277220B1 (en) * 1998-06-23 2001-08-21 Takanari Hamada Steel wire rod and process for producing steel for steel wire rod
US20100034691A1 (en) * 2006-10-31 2010-02-11 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Spring steel wire excellent in fatigue characteristic and wire drawability
EP2017358A2 (en) * 2007-07-20 2009-01-21 Kabushiki Kaisha Kobe Seiko Sho Steel wire material for spring and its producing method
US20090065105A1 (en) * 2007-09-10 2009-03-12 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd) Spring steel wire rod excellent in decarburization resistance and wire drawing workability and method for producing same

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CN105483551A (zh) 2016-04-13
BR102015025517A2 (pt) 2016-05-31
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