EP2518175B1 - Acier à ressorts à haute résistance - Google Patents

Acier à ressorts à haute résistance Download PDF

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Publication number
EP2518175B1
EP2518175B1 EP10839395.0A EP10839395A EP2518175B1 EP 2518175 B1 EP2518175 B1 EP 2518175B1 EP 10839395 A EP10839395 A EP 10839395A EP 2518175 B1 EP2518175 B1 EP 2518175B1
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EP
European Patent Office
Prior art keywords
less
spring
quenching
spring steel
strength
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.)
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Application number
EP10839395.0A
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German (de)
English (en)
Other versions
EP2518175A1 (fr
EP2518175A4 (fr
Inventor
Sayaka Nagamatsu
Tomotada Maruo
Nao Yoshihara
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.)
Kobe Steel Ltd
Original Assignee
Kobe Steel 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
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Publication of EP2518175A1 publication Critical patent/EP2518175A1/fr
Publication of EP2518175A4 publication Critical patent/EP2518175A4/fr
Application granted granted Critical
Publication of EP2518175B1 publication Critical patent/EP2518175B1/fr
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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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • 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
    • 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
    • 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
    • C22C38/02—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
    • C22C38/18—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
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • 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
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/04—Modifying the physical properties of iron or steel by deformation by cold working of the surface
    • C21D7/06—Modifying the physical properties of iron or steel by deformation by cold working of the surface by shot-peening or the like

Definitions

  • the strength of iron and steel materials increases as the hardness increases, and, as the hardness increases, the toughness drops. That is, when the strength of the iron and steel materials increases, the toughness drops, however, as a material for a spring, a fracture property capable of enduring a severe use environment of a spring is required, and it becomes necessary to secure the toughness, or the low temperature toughness in particular which becomes important when used in a cold weather region, even in springs such as a high-strengthened suspension spring and the like.
  • the reason why C is made 0.15% or more is to enhance the quenchability and to secure the strength. Also, the reason why C is made 0.33% or less is to prevent deterioration of the toughness and corrosion fatigue property.
  • the lower limit of the C amount is preferable to be 0.2% or more, more preferably 0.25% or more.
  • the reason why Ti is made 0.005% or more is to miniaturize the former austenite grains after quenching, to improve the strength and proof stress ratio, and to improve the toughness and corrosion fatigue property. By improving the toughness, the sag resistance can be improved. Also, the reason for making Ti 0.10% or less is to prevent precipitation of coarse inclusions (Ti-nitride for example) and to suppress deterioration of the corrosion fatigue property.
  • the lower limit of the Ti amount is preferable to be 0.01% or more (especially preferable to be 0.05% or more), and the upper limit of the Ti amount is preferable to be 0.080% or less, more preferably 0.07% or less.
  • the reason why the carbon equivalent Ceq 1 is made 0.55 or less is to achieve both of the strength and corrosion fatigue property of the spring even when the tempering treatment after quenching is omitted in manufacturing a coil spring by coiling the spring steel. That is, the carbon equivalent Ceq 1 represents the contribution degree of an alloy element exerting influence on the hardness after quenching, the hardness of the core part of the spring can be secured by omitting the tempering treatment after quenching while reducing the value, and high strengthening can be achieved. Also, by suppressing the carbon equivalent Ceq 1 to 0.55 or less, the degree of dependability of the alloy element can be lowered, and stable supply can be ensured more.
  • the carbon equivalent Ceq 1 is preferable to be 0.53 or less, more preferably 0.50 or less.
  • the strength of the specimen was evaluated by measuring the hardness of the specimen with a Rockwell hardness tester using the C scale.
  • the measurement result of the C hardness is shown in Table 2 below. In the present invention, those with HRC of 51 or more are to be evaluated to have passed.
  • No. 1, 4, 13 and 15 are reference examples not satisfying the requirement stipulated in the present invention.
  • No. 2, 3, 5-12, 14 and 33 are the examples satisfying the requirement stipulated in the present invention, and both of the high strength and excellent corrosion fatigue property were achieved. That is, while the carbon equivalent (Ceq 1 ) was suppressed to 0.55 or below, the discharge amount of CO 2 could be reduced because tempering after quenching was omitted, the hardness of the core part could be secured appropriately, and the high strength was achieved. Also, the time until hydrogen embrittlement cracking was long, and the corrosion fatigue property was also improved.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Articles (AREA)
  • Springs (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)

Claims (4)

  1. Acier à ressorts à haute résistance contenant :
    C : 0,15 à 0,33 % (% massique moyen, ci-après identique) ;
    Si : 1 à 3,5 % ;
    Mn : 0,20 à 2,0 % ; et contenant :
    au moins un élément sélectionné parmi un groupe constitué de Ti : 0,005 à 0,10 %, Nb : 0,005 à 0,05 % et V : 0,05 à 0,25 % ;
    Cr : 0,05 à 1,20 % ;
    P : 0,030 % ou moins ;
    S : 0,02 % ou moins ; et
    contenant en outre en option : Ni : 0,05 à 2 % et Cu : 0,05 à 0,50 % ; et
    contenant en outre en option : B : 0,005 % ou moins et/ou Mo : 0,60 % ou moins avec le reste qui est du fer et des impuretés inévitables, dans lequel un carbone équivalent Ceq1 exprimé par une formule (1) ci-dessous est de 0,55 ou moins.
    Ceq1=[C]+0,108x[Si]-0,067x[Mn]+0,024x[Cr]-0,05x[Ni]+0,074x[V]...(1) (dans la formule (1), chaque symbole entre crochets représente la teneur (% massique) de l'élément correspondant.)
  2. Acier à ressorts à haute résistance selon la revendication 1, contenant Ni : 0,15 à 2%.
  3. Acier à ressorts à haute résistance selon la revendication 1, contenant au moins un élément sélectionné parmi un groupe constitué de Ti : 0,035 à 0,10 %, Nb : 0,005 à 0,05 % et V : 0,05 à 0,25 %, dans lequel le nombre granulométrique après trempe est de 7,5 ou plus.
  4. Procédé de fabrication d'un ressort à haute résistance excellent en termes de propriété de fatigue à la corrosion, comprenant les étapes consistant à :
    cintrer à chaud l'acier à ressorts selon l'une quelconque des revendications 1 à 3;
    tremper ; et
    durcir ci-après tout en omettant le revenu.
EP10839395.0A 2009-12-22 2010-12-21 Acier à ressorts à haute résistance Active EP2518175B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2009291143 2009-12-22
PCT/JP2010/073003 WO2011078165A1 (fr) 2009-12-22 2010-12-21 Acier à ressorts à haute résistance

Publications (3)

Publication Number Publication Date
EP2518175A1 EP2518175A1 (fr) 2012-10-31
EP2518175A4 EP2518175A4 (fr) 2015-12-02
EP2518175B1 true EP2518175B1 (fr) 2019-01-23

Family

ID=44195692

Family Applications (1)

Application Number Title Priority Date Filing Date
EP10839395.0A Active EP2518175B1 (fr) 2009-12-22 2010-12-21 Acier à ressorts à haute résistance

Country Status (8)

Country Link
US (2) US20120285585A1 (fr)
EP (1) EP2518175B1 (fr)
JP (2) JP6027302B2 (fr)
KR (1) KR20120084810A (fr)
CN (1) CN102482743B (fr)
BR (1) BR112012014178A2 (fr)
ES (1) ES2709515T3 (fr)
WO (1) WO2011078165A1 (fr)

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JP6033796B2 (ja) * 2012-01-31 2016-11-30 日本発條株式会社 リング状ばねおよびその製造方法
JP2014198874A (ja) * 2013-03-29 2014-10-23 株式会社神戸製鋼所 耐食性と磁気特性に優れた鋼材およびその製造方法
JP6477007B2 (ja) * 2015-02-26 2019-03-06 愛知製鋼株式会社 板ばね及びその製造方法
CN105112774B (zh) * 2015-08-28 2017-12-01 浙江美力科技股份有限公司 高强韧性低中碳微合金风冷硬化弹簧钢及其成形和热处理工艺
CN105088081B (zh) * 2015-08-28 2018-03-13 浙江美力汽车弹簧有限公司 稳定杆的制造工艺
KR101795277B1 (ko) * 2016-06-21 2017-11-08 현대자동차주식회사 내식성이 우수한 고강도 스프링강
KR101795278B1 (ko) * 2016-06-21 2017-11-08 현대자동차주식회사 초고강도 스프링강
CN106011634A (zh) * 2016-07-26 2016-10-12 路望培 一种弹簧机械材料及其制备方法
CN106636896A (zh) * 2016-12-05 2017-05-10 武汉钢铁股份有限公司 一种高淬透性热轧刀板钢
CN107354388B (zh) * 2017-07-25 2019-03-01 西华大学 一种高强高韧贝氏体弹簧钢及其制造方法
JP2020076154A (ja) * 2020-01-07 2020-05-21 日本発條株式会社 懸架装置用ばねの製造方法
CN114134411B (zh) * 2021-10-12 2022-07-29 江阴兴澄特种钢铁有限公司 一种耐低温高强度滚珠丝杠用球化退火钢及其制造方法

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Also Published As

Publication number Publication date
KR20120084810A (ko) 2012-07-30
EP2518175A1 (fr) 2012-10-31
JP2011149089A (ja) 2011-08-04
WO2011078165A1 (fr) 2011-06-30
CN102482743B (zh) 2014-12-24
US20170022580A1 (en) 2017-01-26
ES2709515T3 (es) 2019-04-16
EP2518175A4 (fr) 2015-12-02
US20120285585A1 (en) 2012-11-15
JP2015214754A (ja) 2015-12-03
BR112012014178A2 (pt) 2016-07-05
JP6027302B2 (ja) 2016-11-16
CN102482743A (zh) 2012-05-30

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