EP1905857B1 - Acier à haute résistance et utilisations d'un tel acier - Google Patents

Acier à haute résistance et utilisations d'un tel acier Download PDF

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Publication number
EP1905857B1
EP1905857B1 EP20070116927 EP07116927A EP1905857B1 EP 1905857 B1 EP1905857 B1 EP 1905857B1 EP 20070116927 EP20070116927 EP 20070116927 EP 07116927 A EP07116927 A EP 07116927A EP 1905857 B1 EP1905857 B1 EP 1905857B1
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Prior art keywords
steel
content
application
strength
components
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EP20070116927
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German (de)
English (en)
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EP1905857A2 (fr
EP1905857A3 (fr
Inventor
Serosh Dr. Engineer
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EZM Edelstahlzieherei Mark GmbH
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EZM Edelstahlzieherei Mark GmbH
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Publication of EP1905857A3 publication Critical patent/EP1905857A3/fr
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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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/001—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
    • C22C38/02—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
    • C22C38/06—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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

Definitions

  • the invention relates to a steel having a high tensile strength and uses of such a steel.
  • AFP steels which are standardized in DIN EN 10267 and have a ferrite / pearlitic structure, do not achieve the combination of high strength and fracture deformation characteristics required here.
  • a common disadvantage of the known high-strength materials is moreover that they only reach the respective strength level after an additional tempering treatment.
  • a steel with good deformation properties, but at the same time also with sufficient strength is to be from the EP 1 264 910 A1 known.
  • the known steel contains (in% by weight) in addition to iron and unavoidable impurities as essential components 0.0005 - 0.30% C, 0.001 - 2.0% Si and 0.01 - 3.0% Mn.
  • the known steel may contain a variety of other optional alloying elements to emphasize certain properties of this steel.
  • the known steel can also optionally contain Nb, Ti and V contents with a sum of the contents of these elements of 0.001-0.5% by weight and 0.001-0.20% by weight P and 0.0001. 0.03 wt .-% N are added.
  • the known steel may contain, in total, 0.001 - ⁇ 1.5% by weight Cr, Mo, Ni, Co and / or W.
  • the Cr contents were regularly 0.2 wt.%, while the contents of Nb were 0.02 wt.% on a regular basis.
  • this known steel may optionally contain 0.0005% - 0.005% B, 0.005% - 0.1% Ti and optionally at least one of the elements Ca, Se, Te, Bi and Pb each with contents less than 0.2%.
  • the contents of C, Mn, Ni, Mo, W and Cr of the known steel are to be determined more closely depending on the B content of the steel.
  • the EP 0 725 156 B1 described steel in addition to other alloying elements levels of Cr, N, Mo, Nb may be added to increase its strength.
  • About the influence of Ti on the known steel goes out of the EP 0 725 156 B1 but nothing forth. Also found in the EP 0 735 156 B1 no embodiment from which the effect of Nb, Ti or N in the known steel could be understood.
  • the Cr content of the known steel should preferably be below 0.6%. Accordingly, included in the EP 0 974 678 B1 Illustrated embodiments each Cr contents in the range of less than 0.3%. In addition, none of these embodiments, effective levels of Nb, Ti or N, since these elements according to the in the
  • a steel in addition to iron (in wt .-%) 0.1 - 0.45% C, 0.35 - 1.3% Si, 0.3 - 1.8% Mn, 0.001 - 0.02% S, 0.015-0.04% Al, 0.005-0.04% Nb, 0.006-0.02% N and one or more elements from the group Cr, Mo and Ni, the Cr content being 0.4 -1, 8%, the Mo content is 0.02-1.0%, and the Ni content is 0.1-0.35%.
  • the known steel can also have Ti content of up to 0.005%.
  • the object of the invention was to develop a steel which achieves tensile strength values above 1100 N / mm 2 using alloy additives which are available at low cost and without subsequent tempering treatment.
  • advantageous uses of such a steel should be indicated.
  • a steel according to the invention is composed by a suitable choice of the alloying elements that it converts after cooling in air from the hot rolling heat or forging heat into a fine-grained, tough, martensitic structure and in this way without additional heat treatment high tensile strength values of more than 1100 N. / mm 2 reached.
  • the microstructure of the steel according to the invention can be varied by selecting a suitable cooling rate between a substantially pure martensitic or martensitic, lower bainite fractions and a ferritic-bainitic-martensitic microstructure.
  • a cooling rate of more than 0.5 K / s between 800 and 500 ° C reliably sets up a completely martensitic microstructure or a structure with martensite and lower bainite, while at lower cooling rates the bainite content in the microstructure increases and only at slower cooling rates of less than 0.2 K / s ferrite in the structure occur.
  • thermomechanical hot forming rolling or forging
  • wire or steel bar a subsequent controlled cooling in the temperature range between 800 and 500 ° C with a cooling rate of approx. 0.05 K / s produce a duplex structure consisting of 15-30% ferrite and 70-85% martensite (including lower bainite).
  • the hot-formed semi-finished product can be cooled from forming temperatures between 950 and 1100 ° C. to a cross-sectional equivalent of 2830 mm 2 in air.
  • the C content of a steel according to the invention is at least 0.15% by weight, in terms of the weldability and the ductility of the set hardening structure sure. In this way, a good combination of high strength and ductility is achieved without a subsequent tempering of the structure. At the same time, the C content is limited to a maximum of 0.3 wt% in order to avoid the formation of hot cracks after welding and excessive distortion of the tetragonal texture of the martensite. The latter leads to a reduction in the ductility properties in the unannealed state.
  • the Si content of a steel according to the invention is in the range of 0.1-0.5% by weight in order to avoid additional solidification of the steel matrix and thus to keep the ductility degradation in the unannealed state low.
  • Mn is present in a steel according to the invention in amounts of at least 0.6% by weight in order to achieve sufficient hardenability of the steel with the aid of this inexpensive alloying element. More than 1.8% by weight should not be present in steel according to the invention, otherwise excessive segregation of this alloying element may occur, which would impair the combination of strength and ductility.
  • the effect of Mn used according to the invention in steel according to the invention is optimal when the Mn content is 1.6-1.8% by weight.
  • the presence of Cr in contents of 1.0-1.8% by weight is of particular importance for the steel alloyed according to the invention.
  • Cr an increase in the hardenability of the steel is achieved without the temperature of the transformation into the martensite stage (also the martensite start temperature "Ms" called) to change significantly.
  • Ms martensite start temperature
  • a self-tempering effect of the cure texture due to cooling from the hot working temperatures is achieved, giving the steel of the present invention a good combination of high strength and ductility after cooling from hot working temperatures without further tempering treatment.
  • This effect can be achieved particularly reliably if the Cr content is 1.5-1.8% by weight, in particular 1.5-1.7% by weight.
  • Mo is present in a steel of the present invention at levels of 0.10-0.50 weight percent to extend the conversion range in the martensite and lower bainite levels. With this measure, it is possible to set larger semifinished product dimensions with the desired microstructure constituents which determine the strength and ductility characteristic values obtained according to the invention. At contents of less than 0.1% by weight, this effect does not occur to the desired extent, while contents of more than 0.5% by weight lead to no significant improvement in the properties, but merely unnecessarily increase the cost of the steel according to the invention.
  • the effect of molybdenum used according to the invention is particularly safe if the Mo content is in the range from 0.2 to 0.4% by weight.
  • Steel according to the invention may contain up to 0.50% by weight of nickel to promote the ductility of the steel matrix. At higher levels of Ni, no significant improvements of the steel according to the invention occur for the property profile required according to the invention. Therefore, the Ni content of steel according to the invention should preferably be at most 0.2 wt .-%.
  • Nb at levels of 0.030 - 0.150 wt .-% is also of particular importance.
  • Nb at levels of 0.030 - 0.150 wt .-% is also of particular importance.
  • a refinement of the microstructure is achieved.
  • small amounts of niobium dissolved in the steel matrix broaden the martensite / lower bainite conversion range.
  • no more than 0.150 weight percent Nb should be present in steel of the present invention to avoid excessive precipitation of niobium compounds on the grain boundaries during cooling from hot working temperatures.
  • Optimized effects of Nb in steel according to the invention are achieved when the Nb content is 0.08-0.12% by weight.
  • Ti is present in grades of 0.020-0.060 wt% of steel in accordance with the present invention to assure fine granularity at elevated temperatures. This effect is achieved particularly reliably when the Ti content of the steel according to the invention is 0.025-0.045% by weight.
  • Al is added to steel in accordance with the invention for purposes of deoxidation at levels of 0.010-0.060 wt%.
  • N is added to steels of the present invention at levels of 0.008-0.030 weight percent to facilitate the formation of niobium and titanium nitrides.
  • the precipitates of niobium and titanium nitrides are very effective for grain refinement.
  • P content is set to less than 0.030 wt .-%. At higher P contents, impairment of the ductility properties is to be expected.
  • the manganese sulfides in the steel according to the invention could be stretched too much and form potential break points of the components formed from the steel according to the invention. This danger should be avoided in particular if high-strength pressure-tight components are produced from steel according to the invention. Therefore, the S content of the steel according to the invention is limited to a maximum of 0.030 wt .-%.
  • Steel composed according to the invention has a fine-grained, tough martensitic structure after hot rolling or hot forging followed by cooling in still air. This applies in particular if the alloying ranges for Mn, Cr, Mo, Nb, Ti and Ni, which are each referred to as particularly favorable, are adhered to.
  • Steel according to the invention because of its fine-grained, tough martensite-containing structure, is suitable for pressure-tight components for diesel injection systems which are stressed at pressures of up to 3,000 bar.
  • the low medium-voltage sensitivity of the steel according to the invention makes steel according to the invention particularly suitable for the production of components which are subjected to oscillatory stress in the tensile-swelling and tensile-pressure regions. Components of this type are needed in particular in the automotive industry or generally in the field of the construction of internal combustion engines.
  • steels according to the invention are furthermore particularly suitable for the production of high-strength components, such as sling chains, chain locks, mining chains and chains for securing motorcycles and bicycles, or for the production of fastening elements. like nuts and bolts.
  • components can be produced which are surface-treated.
  • the surface treatment can be carried out as case hardening, nitriding, nitrocarburizing or as laser beam treatment.
  • the correspondingly treated articles may in particular be wear-resistant, pressure-tight components which are subject to oscillatory stress also be used at operating temperatures up to 450 ° C.
  • Another use according to the invention of a steel according to the invention consists in flat products which are punched and deposited in air.
  • a flat product may, for example, be the B-pillar of an automobile body.
  • steel according to the invention is particularly suitable for the production of hot-formed and air-laid tubes and flat bars, which are used, for example, as reinforcement of doors against side impact in passenger and commercial vehicles.
  • steels according to the invention can be used particularly well in general form for the production of hot or cold formed, high strength and generally used in mechanical engineering components.
  • Cold piled tubes or cold rolled flat bars with increased strength can be produced just as well from steels according to the invention.
  • Table 1 shows by way of example a composition of a steel according to the invention. This steel is melted, shed to a billet in the strand and hot rolled to bars and wire. Subsequently, various samples of this steel have been cooled at different rates.
  • the steel according to the invention thus converts from the austenitizing temperature into the martensite stage by suitable cooling and achieves an unexpectedly good combination of strength and fracture deformation characteristics (ductility) because of the fine graininess of the structure and the self-tempering effect during the cooling process.
  • ductility strength and fracture deformation characteristics

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (18)

  1. Acier à haute résistance à la traction, contenant (en % en poids) : C : 0,15 à 0,3 %, Si : 0,1 à 0,5 %, Mn : 0,6 à 1,8 %, Cr : 1,0 à 1,8 %, Mo : 0,10 à 0,50 %, Ni : jusqu'à 0,50 %, Nb : 0,030 à 0,150 %, Ti : 0,020 à 0,060 %, Al : 0,010 à 0,060 %, N : 0,008 à 0,030 %, P : < 0,030 %, S : < 0,030 %,
    le reste étant du fer et des impuretés inévitables.
  2. Acier selon la revendication 1, caractérisé en ce que sa teneur en Cr est de 1,5 à 1,8 % en poids.
  3. Acier selon la revendication 2, caractérisé en ce que sa teneur en Cr est de 1,5 à 1,7 % en poids.
  4. Acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Mn est de 1,6 à 1,8 % en poids.
  5. Acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Mo est de 0,2 à 0,4 % en poids.
  6. Acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Nb est de 0,08 à 0,12 % en poids.
  7. Acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Ti est de 0,025 à 0,045 % en poids.
  8. Acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Ni est au maximum de 0,2 % en poids.
  9. Acier selon l'une des revendications précédentes, caractérisé en ce qu'il a une structure duplex martensitique ferrito - martensitique avec une teneur en ferrite de 15 à 30 % et une teneur en martensite de 70 à 85 %.
  10. Utilisation d'un acier selon l'une des revendications 1 à 9 pour la fabrication de pièces étanches à la pression pour des systèmes d'injection diesel, qui sont soumis à des pressions allant jusqu'à 3000 bars.
  11. Utilisation d'un acier selon l'une des revendications 1 à 9 pour la fabrication de pièces, qui, oscillantes, sont sollicitées par traction - contrainte ondulée et traction - compression.
  12. Utilisation d'un acier selon l'une des revendications 1 à 9 pour la fabrication de pièces à haute résistance, comme élingues, joints de chaînes, chaînes pour l'exploitation minière, ainsi que chaînes pour sécuriser motos et bicyclettes.
  13. Utilisation d'un acier selon l'une des revendications 1 à 9 pour la fabrication d'éléments de fixation.
  14. Utilisation d'un acier selon l'une des revendications 1 à 9 pour la fabrication de pièces à haute résistance, formés à froid, pour automobiles.
  15. Utilisation d'un acier selon l'une des revendications 1 à 9 pour la fabrication d'un pied milieu d'une carrosserie d'automobile.
  16. Utilisation d'un acier selon l'une des revendications 1 à 9 pour la fabrication de tubes ou de barres plates façonnés à chaud et mis à l'air.
  17. Utilisation selon la revendication 16, caractérisée en ce que les tubes ou les barres plates sont employés comme renforcement antichoc latéral de portes de voitures particulières et utilitaires.
  18. Utilisation d'un acier selon l'une des revendications 1 à 9 pour la fabrication de pièces à haute résistance, formées à chaud ou à froid, employées dans l'industrie mécanique, générale.
EP20070116927 2006-09-29 2007-09-21 Acier à haute résistance et utilisations d'un tel acier Active EP1905857B1 (fr)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
DE102006046481 2006-09-29

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EP1905857A2 EP1905857A2 (fr) 2008-04-02
EP1905857A3 EP1905857A3 (fr) 2010-03-03
EP1905857B1 true EP1905857B1 (fr) 2013-08-14

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ES (1) ES2430839T3 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102016108633A1 (de) * 2016-05-10 2017-11-30 Benteler Steel/Tube Gmbh Kraftstoffeinspritzleitung und rohrförmiger Leitungskanal

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102008052885A1 (de) * 2008-10-23 2010-04-29 Deutsche Edelstahlwerke Gmbh Einsatzstahl
JP6110840B2 (ja) 2014-12-08 2017-04-05 日本発條株式会社 スタビライザの製造方法
JP6053746B2 (ja) 2014-12-08 2016-12-27 日本発條株式会社 スタビライザ
CN105063514B (zh) * 2015-09-07 2017-05-10 宁波瑞国精机工业有限公司 一种车用铁链销及其加工方法
CN105543678B (zh) * 2015-12-21 2017-04-05 武钢集团昆明钢铁股份有限公司 一种含硼高强度免退火紧固件用钢盘条及其制备方法
WO2020058269A1 (fr) 2018-09-18 2020-03-26 Ezm Edelstahlzieherei Mark Gmbh Acier pour le durcissement de surface ayant une dureté superficielle élevée et une structure de base ductile fine
CN110359007B (zh) * 2019-07-16 2021-05-28 苏州新凌高强度紧固件有限公司 一种20MnTiB紧固件的热处理方法
CN112795854A (zh) * 2020-12-23 2021-05-14 石家庄钢铁有限责任公司 高强度紧固件螺栓用钢及其生产方法
CN112626308A (zh) * 2020-12-25 2021-04-09 常州东方特钢有限公司 一种通过加入NbN生产的高品质不对称球扁钢的生产工艺
CN113699437A (zh) * 2021-06-25 2021-11-26 武汉钢铁有限公司 车厢板用热连轧双相耐磨钢及生产方法

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2729974B1 (fr) 1995-01-31 1997-02-28 Creusot Loire Acier a haute ductilite, procede de fabrication et utilisation
DE19511656C2 (de) 1995-03-30 1997-11-27 Wieland Werke Ag Partiell feuerverzinntes Band
WO1998050594A1 (fr) * 1997-05-08 1998-11-12 The Timken Company Compositions d'acier et procedes de traitement destines a produire de composants carbures formes a froid et ayant des microstructures a grain fin
FR2781506B1 (fr) 1998-07-21 2000-08-25 Creusot Loire Procede et acier pour la fabrication d'une enceinte chaudronnee travaillant en presence d'hydrogene sulfure
JP4050829B2 (ja) * 1998-07-30 2008-02-20 新日本製鐵株式会社 転動疲労特性に優れた浸炭材
US6866725B2 (en) 2000-02-28 2005-03-15 Nippon Steel Corporation Steel pipe excellent in formability and method of producing the same
US7081174B2 (en) * 2002-04-30 2006-07-25 Sanyo Special Steel Co., Ltd. Process for producing steel products having improved grain size properties and machinability
FR2847273B1 (fr) * 2002-11-19 2005-08-19 Usinor Piece d'acier de construction soudable et procede de fabrication

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102016108633A1 (de) * 2016-05-10 2017-11-30 Benteler Steel/Tube Gmbh Kraftstoffeinspritzleitung und rohrförmiger Leitungskanal

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ES2430839T3 (es) 2013-11-22
EP1905857A3 (fr) 2010-03-03

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