EP1780293A2 - Procédure de fabrication de la matière brute de l'acier par déformer ä chaud - Google Patents

Procédure de fabrication de la matière brute de l'acier par déformer ä chaud Download PDF

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Publication number
EP1780293A2
EP1780293A2 EP06022284A EP06022284A EP1780293A2 EP 1780293 A2 EP1780293 A2 EP 1780293A2 EP 06022284 A EP06022284 A EP 06022284A EP 06022284 A EP06022284 A EP 06022284A EP 1780293 A2 EP1780293 A2 EP 1780293A2
Authority
EP
European Patent Office
Prior art keywords
steel
titanium
starting material
manganese
boron
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.)
Granted
Application number
EP06022284A
Other languages
German (de)
English (en)
Other versions
EP1780293B2 (fr
EP1780293B1 (fr
EP1780293A3 (fr
Inventor
Frauendorfer Robert
Kinsinger Dr. Volker
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.)
Saarstahl AG
Original Assignee
Saarstahl AG
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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Application filed by Saarstahl AG filed Critical Saarstahl AG
Priority to PL06022284T priority Critical patent/PL1780293T3/pl
Publication of EP1780293A2 publication Critical patent/EP1780293A2/fr
Publication of EP1780293A3 publication Critical patent/EP1780293A3/fr
Application granted granted Critical
Publication of EP1780293B1 publication Critical patent/EP1780293B1/fr
Publication of EP1780293B2 publication Critical patent/EP1780293B2/fr
Not-in-force 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • 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
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/04—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
    • C22C38/06—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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—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

Definitions

  • the invention relates to a method of producing a starting material from steel, for example for producing wire rod and bar steel with high strength and toughness by hot working.
  • the prior art knows a number of methods for producing steel components with high strength and high toughness. Starting from wire rod or bar steel cold forming and thermoforming processes are known.
  • the mechanical properties are set by cold work hardening during forming. To achieve high strength, high degrees of deformation are required. This is at the expense of toughness, so that the cold forming reaches its limits where the toughness of the component as a result of work hardening is no longer sufficient and thus results in an unfavorable strength-toughness ratio.
  • tempered steels according to DIN EN 10083 are used, in which, depending on the thickness of the component, it is possible, via the heat treatment, to set strengths of more than 1000 MPa for fracture constrictions of more than 45%.
  • the ratio of yield strength to strength can be at least 0.8.
  • manganese / silicon dual-phase steels are used to produce cold-formed components of high strength from rolled material State of the art.
  • these steels are not suitable for use with required strengths greater than 1000 MPa and high yield ratio above 0.8; They also require to set a certain initial strength and toughness in the starting material, a thermomechanical hot rolling and a parked on this initial strength cold work or strain hardening, so as to set a microstructure of a ferrite matrix with embedded Martensit and Perlitinseln.
  • High-strength steel components can be produced, starting from hot-rolled starting material, for example wire rod or bar steel, by cold forming and, if appropriate, tempering, also by hot forming.
  • thermoforming parts can be used after forming a heat treatment to adjust the mechanical properties. This is the classic application of tempered steels. However, since they require additional heat treatment, the already mentioned high cost and environmental impact arise. To avoid this heat treatment, hardening from forging heat is known. It eliminates heating to austenitizing temperature and quenching. However, low alloyed steels require a final tempering to provide the required performance properties, especially the necessary toughness.
  • Another material variant associated with forging heat is the so-called direct-hardening soft-martensitic steels with carbon contents of up to 0.1% and matched chromium, boron and manganese contents, which do not require tempering. These steels contain 0.05% carbon or even 0.10% carbon in the absence of chromium.
  • a disadvantage of these steels is that a high cooling rate is required for adjusting the martensitic microstructure. This requires additional facilities on the Umformaggregat for oil or water quenching, which eat up a part of the cost savings. Furthermore, the high cooling rate causes complex parts or those with large differences in wall thickness tend to delay and the structure and the mechanical properties can be inhomogeneous over the cross section.
  • AFP steels i. precipitation-hardening ferritic-pearlitic steels developed (for example according to DIN EN 10267). These obtain their mechanical properties through a controlled cooling from the thermoforming temperature and the excretion of carbonitrides of the elements titanium, vanadium and niobium. These steels are less prone to distortion than the blacksmiths site or bainite. Compared to tempered steels, however, they have a lower yield strength and lower toughness. At strengths of 800 to 1000 MPa only yield strengths of up to 600 MPa are achieved. For applications in the high load range, which require strengths around 1000 MPa at yield strengths above 750 MPa, the conventional AFP steels are therefore unsuitable.
  • European Patent Application 1 408 131 A1 a low carbon precipitation hardening ferritic-perlitic steel having 0.12 to 0.45% carbon, 0.10 to 1.00% silicon, 0.50 to 1.95% manganese, 0.005 to 0.060% sulfur, 0.004 to 0.050% aluminum, 0.004 to 0.050% titanium, to 0.60% chromium, to 0.60% niobium, 0.10 to 0.40% vanadium, and 0.015 to 0.040% nitrogen, balance including iron due to melting.
  • This steel needs to develop its mechanical properties only from its forming temperature of 950 to 1250 ° C with a cooling rate of at least 0.2 ° C / s, for example, to be cooled in still air.
  • the analysis specifications and defined parameters during heating to the forming temperature and during cooling must be strictly adhered to.
  • the invention is directed to a method with which a high strength and high toughness and a high ratio of yield strength to strength can be achieved without a heat treatment.
  • According to the invention can be in a steel with 0.08 to 0.25% carbon, up to 1% silicon, 0.5 to 2.5% manganese, up to 0.035% phosphorus, to 0.055% sulfur, 0.1 to 1.5 % Chromium, 0.1 to 0.5% molybdenum, 0.2 to 1.5% nickel, to 0.06% aluminum, 0.0010 to 0.006% boron, each to 0.04% vanadium, niobium and titanium, up to 0.5% copper and up to 0.010% nitrogen, the remainder being iron, including any impurities caused by melting, by adjusting a martensitic-bainitic structure by mere hot working and controlled cooling.
  • the said elements, preferably titanium, are required for the setting of nitrogen. This is necessary for the boron hardenability enhancing effect.
  • the alloy composition and the cooling rate adjust the mechanical properties.
  • a bainitic-martensitic mixed structure On cooling from the deformation temperature of about 1000 to 1300 ° C, a bainitic-martensitic mixed structure, the proportion of ferrite and perlite should not exceed 10% in total. Cooling from the forming heat with gas, water or oil is possible but not required; In order to adjust the bainitic-martensitic microstructure, cooling on or with air is sufficient. A cooling with moving air is to be preferred, as this ensures the preferred minimum cooling rate of 0.3 ° C / s.
  • the use of static or moving air is preferable to other refrigerants, since the environment is then not contaminated by vapors, no additional auxiliaries such as oil or gas and no disposal units such as filters, tanks and catch basins are required.
  • the cooling rate should be at least 0.3 ° C / s in the temperature range between about 1000 and 610 ° C.
  • the steel then has not only high toughness after cooling from the final temperature of hot working to room temperature, but also high strength. The ratio of yield strength to strength is also high.
  • the inventively cooled from the deformation heat starting material is readily suitable for cold forming.
  • strain hardening tensile strengths of more than 1200 MPa can be achieved at yield strengths above 1050 MPa.
  • the ratio of yield strength to strength is above 0.85.
  • the high toughness is evident in fracture necking values of above 40% and elongations at break above 12%.
  • the mechanical properties are therefore better than those of conventional steels or dual-phase steels.
  • the inventively cooled from the deformation heat starting material is also suitable in turn as a starting material for hot forming.
  • a starting material for hot forming In such - second - hot working again arise the original mechanical properties without the need for quenching in water or oil when the cooling conditions of the invention are met.
  • the tendency to warp is lower because of the milder deterrent conditions.
  • higher strengths and, in particular, significantly higher yield strengths result.
  • precipitation hardening by carbonitrides is not strength-determining for the primary material according to the invention, a larger window results in the setting of the analysis and in particular in the conditions of thermoforming in comparison to newer AFP steels.
  • a steel which contains at least 0.10% carbon, 0.3% silicon, 1% manganese, 0.2% chromium, 0.2% nickel, 0.2% molybdenum, 0.0015% is particularly suitable. Boron, 0.014% titanium, single or side by side.
  • the steel individually or next to each other - also in each case at most 0.24% carbon, 2% manganese, 0.020% phosphorus, 0.045% sulfur, 1.4% chromium, 1.4% nickel, 0.4% molybdenum, 0 , 05% aluminum, 0.038% titanium, 0.02% vanadium, 0.02% niobium, 0.3% copper, 0.005% boron and 0.010% nitrogen.
  • a steel refined by the LD process was hot rolled into 15 mm diameter wire, cooled from the rolling heat of accelerated air, and then cold drawn to a final diameter of 14 mm.
  • the steel was made 0.205% carbon 0.56% silicon 1.62% manganese 0.011% phosphorus 0.01% sulfur 0.54% chrome 0.32% molybdenum 0.22% nickel 0.03% aluminum 0.0038% boron 0.036% titanium 0.002% vanadium 0.002% niobium 0.0044% Nitrogen, rest iron including contaminants due to melting.
EP06022284.1A 2005-10-28 2006-10-25 Procédure de fabrication de la matière brute de l'acier par déformer ä chaud Not-in-force EP1780293B2 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
PL06022284T PL1780293T3 (pl) 2005-10-28 2006-10-25 Sposób wytwarzania materiału wyjściowego ze stali za pomocą obróbki plastycznej na gorąco

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
DE102005052069.3A DE102005052069B4 (de) 2005-10-28 2005-10-28 Verfahren zum Herstellen von Vormaterial aus Stahl durch Warmverformen

Publications (4)

Publication Number Publication Date
EP1780293A2 true EP1780293A2 (fr) 2007-05-02
EP1780293A3 EP1780293A3 (fr) 2007-05-30
EP1780293B1 EP1780293B1 (fr) 2013-09-18
EP1780293B2 EP1780293B2 (fr) 2017-11-08

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ID=37714952

Family Applications (1)

Application Number Title Priority Date Filing Date
EP06022284.1A Not-in-force EP1780293B2 (fr) 2005-10-28 2006-10-25 Procédure de fabrication de la matière brute de l'acier par déformer ä chaud

Country Status (4)

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EP (1) EP1780293B2 (fr)
DE (1) DE102005052069B4 (fr)
ES (1) ES2439900T3 (fr)
PL (1) PL1780293T3 (fr)

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2009026881A1 (fr) 2007-08-27 2009-03-05 Georgsmarienhütte Gmbh Acier pour produire des pièces de machines mises en forme à l'état solide
EP2199422A1 (fr) 2008-12-15 2010-06-23 Swiss Steel AG Acier renforcé à précipitation pauvre en carbone pour des applications de frappe à froid
EP3168312A1 (fr) * 2015-11-16 2017-05-17 Deutsche Edelstahlwerke GmbH Acier inoxydable de construction comprenant un joint bainitique, pièce forgée ainsi fabriquée et procédé de fabrication d'une pièce forgée
CN112553530A (zh) * 2020-12-04 2021-03-26 安阳钢铁股份有限公司 一种低屈强比700MPa高强度桥梁钢及其制造方法
WO2022253912A1 (fr) 2021-06-02 2022-12-08 Ascometal France Holding Sas Pièce en acier mise en forme à chaud et procédé de fabrication
WO2023014332A1 (fr) * 2021-08-04 2023-02-09 Ti̇rsan Kardan Sanayi̇ Ve Ti̇caret Anoni̇m Şi̇rketi̇ Acier micro-allié à haute résistance
EP4296393A1 (fr) * 2022-06-23 2023-12-27 Saarstahl Aktiengesellschaft Acier allié trempant au bore, en particulier acier pour trempe et revenu

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Publication number Priority date Publication date Assignee Title
DE102008004371A1 (de) * 2008-01-15 2009-07-16 Robert Bosch Gmbh Bauelement, insbesondere eine Kraftfahrzeugkomponente, aus einem Dualphasen-Stahl
ES2391312T3 (es) 2008-03-10 2012-11-23 Swiss Steel Ag Producto longitudinal laminado en caliente y procedimiento para su fabricación
CN103725954B (zh) * 2013-12-16 2017-01-04 泰州俊宇不锈钢材料有限公司 一种高强度耐腐蚀钢丝及其制造工艺
CN113699452B (zh) * 2021-08-30 2023-03-10 宝武集团马钢轨交材料科技有限公司 一种有轨电车弹性车轮轮箍用钢及其热处理方法和生产方法
DE102022110466A1 (de) 2022-04-29 2023-11-02 Hirschvogel Holding GmbH Verfahren zur Herstellung eines Massivumformbauteils und Massivumformbauteil hergestellt mit einem solchen Verfahren

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US4812182A (en) 1987-07-31 1989-03-14 Hongsheng Fang Air-cooling low-carbon bainitic steel
JPH09263884A (ja) 1996-03-28 1997-10-07 Kobe Steel Ltd 耐孔明き腐食性および圧壊特性に優れた高強度熱延鋼板、および高強度亜鉛系めっき鋼板並びにそれらの製造方法
CN1451776A (zh) 2003-04-30 2003-10-29 清华大学 锰－硅－铬系空冷粒状贝氏体/铁素体复相钢
CN1477226A (zh) 2003-08-01 2004-02-25 清华大学 中低碳锰系空冷贝氏体钢

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FR2741632B1 (fr) † 1995-11-27 1997-12-26 Ascometal Sa Acier pour la fabrication d'une piece forgee ayant une structure bainitique et procede de fabrication d'une piece
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US4812182A (en) 1987-07-31 1989-03-14 Hongsheng Fang Air-cooling low-carbon bainitic steel
JPH09263884A (ja) 1996-03-28 1997-10-07 Kobe Steel Ltd 耐孔明き腐食性および圧壊特性に優れた高強度熱延鋼板、および高強度亜鉛系めっき鋼板並びにそれらの製造方法
CN1451776A (zh) 2003-04-30 2003-10-29 清华大学 锰－硅－铬系空冷粒状贝氏体/铁素体复相钢
CN1477226A (zh) 2003-08-01 2004-02-25 清华大学 中低碳锰系空冷贝氏体钢

Cited By (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2009026881A1 (fr) 2007-08-27 2009-03-05 Georgsmarienhütte Gmbh Acier pour produire des pièces de machines mises en forme à l'état solide
EA017741B1 (ru) * 2007-08-27 2013-02-28 Георгсмариенхютте Гмбх Сталь для получения деталей машин путем объемной деформации
EP2199422A1 (fr) 2008-12-15 2010-06-23 Swiss Steel AG Acier renforcé à précipitation pauvre en carbone pour des applications de frappe à froid
EP3168312A1 (fr) * 2015-11-16 2017-05-17 Deutsche Edelstahlwerke GmbH Acier inoxydable de construction comprenant un joint bainitique, pièce forgée ainsi fabriquée et procédé de fabrication d'une pièce forgée
WO2017085072A1 (fr) * 2015-11-16 2017-05-26 Deutsche Edelstahlwerke Gmbh Acier de construction fin présentant une structure bainitique, pièce forgée fabriquée à partir de celui-ci et procédé pour la fabrication d'une pièce forgé
KR20180071357A (ko) * 2015-11-16 2018-06-27 도이체 에델스탈베르케 스페시알티 스틸 게엠베하 운트 코. 카게 베이나이트 조직의 고-등급 구조용 강, 베이나이트 조직의 고-등급 구조용 강으로 제조된 단조품 및 단조품 제조 방법
CN112553530A (zh) * 2020-12-04 2021-03-26 安阳钢铁股份有限公司 一种低屈强比700MPa高强度桥梁钢及其制造方法
CN112553530B (zh) * 2020-12-04 2022-03-11 安阳钢铁股份有限公司 一种低屈强比700MPa高强度桥梁钢及其制造方法
WO2022253912A1 (fr) 2021-06-02 2022-12-08 Ascometal France Holding Sas Pièce en acier mise en forme à chaud et procédé de fabrication
FR3123659A1 (fr) 2021-06-02 2022-12-09 Ascometal France Holding Sas Pièce en acier mise en forme à chaud et procédé de fabrication
WO2023014332A1 (fr) * 2021-08-04 2023-02-09 Ti̇rsan Kardan Sanayi̇ Ve Ti̇caret Anoni̇m Şi̇rketi̇ Acier micro-allié à haute résistance
EP4296393A1 (fr) * 2022-06-23 2023-12-27 Saarstahl Aktiengesellschaft Acier allié trempant au bore, en particulier acier pour trempe et revenu
WO2023247214A1 (fr) * 2022-06-23 2023-12-28 Saarstahl Aktiengesellschaft Acier allié au bore, en particulier acier traité thermiquement

Also Published As

Publication number Publication date
PL1780293T3 (pl) 2014-03-31
EP1780293B2 (fr) 2017-11-08
ES2439900T3 (es) 2014-01-27
DE102005052069A1 (de) 2007-05-03
DE102005052069B4 (de) 2015-07-09
EP1780293B1 (fr) 2013-09-18
EP1780293A3 (fr) 2007-05-30

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