EP2553133A2 - Acier, produit plat en acier, élément en acier et procédé de fabrication d'un élément en acier - Google Patents

Acier, produit plat en acier, élément en acier et procédé de fabrication d'un élément en acier

Info

Publication number
EP2553133A2
EP2553133A2 EP11711594A EP11711594A EP2553133A2 EP 2553133 A2 EP2553133 A2 EP 2553133A2 EP 11711594 A EP11711594 A EP 11711594A EP 11711594 A EP11711594 A EP 11711594A EP 2553133 A2 EP2553133 A2 EP 2553133A2
Authority
EP
European Patent Office
Prior art keywords
steel
component
content
flat
product
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
EP11711594A
Other languages
German (de)
English (en)
Other versions
EP2553133B1 (fr
Inventor
Thomas Gerber
Ilse Heckelmann
Thomas Heller
Julia Mura
Martin Norden
Nicolas Vives Diaz
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.)
ThyssenKrupp Steel Europe AG
Original Assignee
ThyssenKrupp Steel Europe 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
Application filed by ThyssenKrupp Steel Europe AG filed Critical ThyssenKrupp Steel Europe AG
Priority to PL11711594T priority Critical patent/PL2553133T3/pl
Priority to EP11711594.9A priority patent/EP2553133B1/fr
Publication of EP2553133A2 publication Critical patent/EP2553133A2/fr
Application granted granted Critical
Publication of EP2553133B1 publication Critical patent/EP2553133B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing 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
    • C21D6/00—Heat treatment 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
    • C21D9/46—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
    • C22C38/06—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
    • C22C38/12—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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a steel, a flat steel product, a steel component produced therefrom and a method for producing a steel component.
  • hot-press hardened components typically have only a low ductility from MnB steels (A 80 : approx. 5 - 6%).
  • body parts are made of so-called "tailored blanks". These are sheet metal blanks made from blanks
  • a "tailored blank" is made available for the production of a B pillar of a car body, the area of which associated with the upper part of the B pillar consists of a 22MnB5 steel.
  • the foot of the B-pillar In the foot of the B-pillar
  • One eligible steel is H340LAD
  • the regions consisting of the ductile material in the critical region of the respective component generally have to have a higher sheet thickness in order to be able to absorb the loads that are exerted on the component during normal operation. This in turn has a correspondingly higher weight for the overall component.
  • Components as they are installed in particular in motor vehicle bodies to produce from a steel sheet material, in the high strength with good elongation properties
  • a first development direction to meet this requirement is aimed at optimizing the manufacturing process.
  • a steel grade with a martensitic structure and improved elongation at break should be able to be produced.
  • An example of this procedure is described in EP 1 642 991 B1 and provides for a high and then a slower cooling rate until the martensite stop temperature is reached. In this way, a self-tempered martensite is produced, which has an improved elongation at break.
  • An alternative development direction is the
  • the flat steel product to be formed to the respective component is heated to a temperature lying between the A ci and the A c3 temperature at which the steel has a two-phase structure.
  • the finished component has a lower martensite content and higher proportions of more ductile phases, such as ferrite or austenite, after cooling compared to conventionally austenitized and hardened components.
  • Zn-based coating of the flat steel product is to be selected, from which the component is formed.
  • the processed flat steel product is after
  • the steel in question (in% by weight) 0.15 - 0.25% C, 1.0 - 1.5% Mn, 0.1 - 0.35% Si, max. 0.8% Cr, in particular 0.1-0.4% Cr, max. 0.1% Al, up to 0.05% Nb, in particular max. 0.03% Nb, up to 0.01% N, 0.01-0.07% Ti, ⁇ 0.05% P, especially ⁇ 0.03% P, ⁇ 0.03% S,> 0.0005 to ⁇ 0.008% B, in particular at least 0.0015% B, and the remainder
  • the object of the invention was to provide a steel in which it is ensured with high reliability that a component manufactured from it has in each case high strength values and an increased elongation at break. Similarly, a flat steel product made using this steel, a steel component made therefrom, and an apparatus for making such
  • the solution according to the invention of the abovementioned object is that such a steel component is designed according to claim 9.
  • the invention is based on the recognition that, by selecting a suitable alloy and setting a suitable microstructure composition, it is possible to provide a steel which, after austenitization, thermoforming and hardening, has a high strength of at least 1000 MPa and an elongation at break Aso, in each case safely above 6%.
  • the steel according to the invention contains (in% by weight) 0.15-0.40% C, 1.0-2.0% Mn, 0.2-1.6% Al, up to 1.4% Si, wherein the sum of the contents of Si and Al is 0.25 - 1.6%, up to 0.10% P, 0 - 0.03% S, up to 0.5% Cr, up to 1.0% Mo , up to 0.01% N, up to 2.0% Ni, 0.012-0.04 Nb, up to 0.40% Ti,
  • An inventive flat steel product has
  • At least one area which consists of a steel according to the invention. So can one
  • steel according to the invention is produced, while another area is made of a different steel.
  • the area produced by the steel according to the invention of the tailored blanks according to the invention forms on the finished, from the steel flat product produced steel component then a high-strength area in which a high strength combined with a good elongation at break. It is exactly like that
  • a steel component according to the invention is correspondingly characterized in that it consists of a steel according to the invention at least in one region and that its structure in the region of the high-strength steel according to the invention is composed of arsenite, austenite and up to 20 area% ferrite.
  • This flat steel product is then heated to a temperature of 780-950 ° C.
  • the austenite content is thus adjusted to at least 80% in order to produce, after thermoforming, a steel according to the invention with a structure consisting of martensite, austenite and up to 20 area% of ferrite.
  • the required hold time is typically 2 to 10 minutes.
  • the flat steel product is usually transported to a thermoforming mold to be thermoformed there to become. Too strong during transport
  • thermoforming itself can be carried out in a conventional manner as compression molding.
  • the steel component After the hot forming, the steel component is cooled down so rapidly that the steel component obtained after cooling has a structure consisting of martensite,
  • Austenite and up to 20 area% ferrite are in the range of at least 25 ° C / s.
  • Hot forming and cooling can be carried out in one or two stages.
  • the component according to the invention when the respective processed flat steel product has been austenitized within the abovementioned temperatures, the component according to the invention, after hot forming and accelerated cooling in the region consisting of a steel according to the invention, has a structure which is characterized by a combination of a hard phase ( Martensite) and at least one more ductile phase (austenite and ferrite).
  • the ferrite content is predetermined by the invention
  • Composition of the processed steel limited to 20 area%, as an improvement in the elongation values and a Increasing the energy absorption by austenite are preferred.
  • austenite By the combination of martensite, austenite and a maximum of 20 area% ferrite are the mechanical
  • the invention sought after is particularly safe
  • the austenite content of the structure of the component according to the invention is at least 2 area%.
  • the tensile strength of a component made from steel according to the invention should not be below 1000 MPa in the region of its high-strength range.
  • the steel alloy according to the invention contains a C content of at least 0.15% by weight. In order at the same time to ensure sufficient welding suitability for practice, the C content of the steel according to the invention is limited to 0.4% by weight at the top.
  • Microstructure is of particular importance for the alloying elements Mn, Si and Al of a steel used according to the invention, since they stabilize the austenite at room temperature.
  • Austenitic agent by minimizing the Ac 3 temperature of the steel. The result is a fabric that after the
  • Hot forming consists essentially of austenite and martensite.
  • the Mn content is limited to a maximum of 2% by weight.
  • Silicon is present in the steel of the present invention at levels of up to 1.4% by weight. It affects the hardenability and serves in the melting of the steel of the component according to the invention as a deoxidizer. At the same time, Si increases the yield strength, stabilizes the ferrite and the austenite at room temperature, and prevents unwanted
  • the Si content of a steel of the present invention is limited to 1.4% by weight.
  • Aluminum contributes to the stabilization of the ferrite and the austenite in the steel according to the invention similar to Si
  • thermoformed structure preferably at least 2 area% stabilized in the thermoformed structure.
  • Mo may be present in a steel of the invention at levels of up to 1.0% by weight.
  • the presence of Mo promotes martensite formation and improves the toughness of the steel.
  • a too high Mo content can be present in a steel of the invention at levels of up to 1.0% by weight.
  • P can be used in amounts of up to 0.10 wt .-% to increase the yield strength and thus to secure the mechanical
  • Precipitate formation eg of Ti carbonitrides.
  • Ti binds N to TiN promoting the efficiency of B in terms of conversion behavior. This effect can be ensured by the Ti content of the steel according to the invention being the condition
  • the boron present in the steel according to the invention stabilizes the mechanical properties for a wide temperature range of
  • N stabilizes the austenite and increases the yield strength of a steel according to the invention. If de present in the alloy steel according to the invention is not completely bound by Ti, it reacts in combination with boron to boron nitrides. These boron nitrides cause a grain refining of the initial microstructure and thus a refining of the martensitic thermoformed microstructure. As a result, the susceptibility of a
  • N is to be used in combination with B by the formation of boron nitrides for grain refining and strength increase, If necessary, the N content which is not bound to Ti can be adjusted in a targeted manner such that, in the case that applies to its Ti content
  • Nb increases the yield strength by means of composite steel according to the invention
  • Carbide precipitation and Austenitkornfeinung causes a fine arsenite structure, which has a high resistance to crack propagation.
  • Nb precipitates may act as hydrogen traps, thereby reducing susceptibility to hydrogen-induced cracking.
  • Ni in amounts of up to 2.0% by weight contributes to increasing the yield strength and the elongation at break.
  • the S content of the steel of a component according to the invention is limited to max. 0.03 wt .-% limited because S a strong negative impact on the weldability and the Possibilities of surface refinement has. Also, this restriction is intended to make the formation of harmful,
  • Ca may be added to the steel of this invention at levels of up to 0.0050% by weight to effect sulfide form control.
  • Ca sulphides form which, in contrast to the otherwise possibly arising elongate MnS precipitates, promote a higher isotropy of the properties of the steel according to the invention.
  • the steel component according to the invention may be coated on its free surface with a protective coating against oxidation. This is preferably already present on the flat steel product from which the component
  • the protective cover can be designed so that it protects against scale formation during heating and thermoforming and / or corrosion during processing or in practical use.
  • metallic, organic or inorganic coatings as well as combinations of these coatings can be used.
  • the coating of the flat steel product can by
  • Hot dip process advantageously be preceded by a pre-oxidation.
  • an oxide layer which is 10-1000 nm thick is selectively produced on the flat steel product, with particularly good coating qualities resulting when the oxide layer is 70-500 nm thick.
  • the setting of the oxide layer thickness takes place in one
  • Oxidation chamber as for example from the
  • WO 2007/124781 AI is known. Before immersion in the melt or before surface refinement, the iron oxide layer is reduced by hydrogen of the annealing atmosphere. It can on the surface and up to a depth of 10 ⁇ oxides of the alloying elements
  • the electrolytic coating is particularly suitable for applying the respective coating. Especially good
  • Coating material Zn, ZnFe, ZnMn, ZnNi systems or their combination can be used.
  • PVD Physical Vapor Deposition
  • CVD Chemical Vapor Deposition
  • Coil coating plants in the coil coating, spraying or dipping method be appropriate.
  • Typical thicknesses of the coatings which can be produced by the processes described here are in the range from 1 to 15 ⁇ m.
  • the invention is based on
  • the blanks consisting of the steels El-E6 and V are in the uncoated state warmed in each case to a temperature in the range of 880-925 ° C temperature, then placed in a thermoforming mold and then hot-formed into a component.
  • each of the boards thermoformed components are each with A cooling rate of at least 25 ° C / s has been cooled to room temperature so quickly that hardened structures have formed in it.
  • the samples were additionally subjected to a cathodic dip coating treatment including a 20 minute bake at 170 ° C.
  • Test stamps have been charged.
  • the "energy intake in the 3-point bending test” mentioned above is the energy uptake until it breaks. Likewise are in
  • the components consisting of the steels El - E6 according to the invention have a consistently high residual deformation capacity characterized by a high value of the product of tensile strength R m and elongation A 80 and, consequently, high energy absorption capacity

Landscapes

  • 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 Articles (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Forging (AREA)

Abstract

L'invention concerne un acier, un produit plat en acier, un élément en acier fabriqué à partir de ce dernier par formage à chaud et trempe subséquente, et un procédé de fabrication d'un tel élément en acier. Pour garantir avec une fiabilité élevée qu'un élément fabriqué en utilisant ledit acier possède des valeurs de résistance respectives élevées et un allongement à la rupture élevé, l'acier de l'invention contient (en % en poids) C: 0,15 à 0,40 %, Mn: 1,0 à 2,0 %, Al: 0,2 à 1,6 %, Si: 0 à 1,4 %, somme des teneurs en Si et Al: 0,25 à 1,6 %, P: 0 à 0,10 %, S: 0 à 0,03 %, Cr: 0 à 0,5 %, Mo: 0 à 1,0 %, N : 0 à 0,01 %, Ni: 0 à 2,0 %, Nb: 0,012 à 0,04 %, Ti: 0 à 0,40 %, B: 0,0010 à 0,0050 %, Ca: 0 à 0,0050 %, le reste étant du fer et des impuretés inévitables. Pour fabriquer un élément selon l'invention, un produit plat composé de l'acier selon l'invention est chauffé à une température comprise entre 780 et 950 °C puis façonné à chaud pour obtenir l'élément. L'élément ainsi obtenu est ensuite soumis à un refroidissement accéléré, de manière à présenter, suite à ce refroidissement, une structure qui se situe au minimum dans le domaine de l'acier à haute résistance, constituée de martensite, d'austénite et jusqu'à 20 % en surface de ferrite.
EP11711594.9A 2010-04-01 2011-04-01 Acier, produit plat en acier, élément en acier et procédé de fabrication d'un élément en acier Active EP2553133B1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
PL11711594T PL2553133T3 (pl) 2010-04-01 2011-04-01 Stal, płaski produkt stalowy, element stalowy i sposób wytwarzania elementu stalowego
EP11711594.9A EP2553133B1 (fr) 2010-04-01 2011-04-01 Acier, produit plat en acier, élément en acier et procédé de fabrication d'un élément en acier

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
EP10158923A EP2374910A1 (fr) 2010-04-01 2010-04-01 Acier, produit plat en acier, composant en acier et procédé de fabrication d'un composant en acier
PCT/EP2011/055117 WO2011121118A2 (fr) 2010-04-01 2011-04-01 Acier, produit plat en acier, élément en acier et procédé de fabrication d'un élément en acier
EP11711594.9A EP2553133B1 (fr) 2010-04-01 2011-04-01 Acier, produit plat en acier, élément en acier et procédé de fabrication d'un élément en acier

Publications (2)

Publication Number Publication Date
EP2553133A2 true EP2553133A2 (fr) 2013-02-06
EP2553133B1 EP2553133B1 (fr) 2014-08-27

Family

ID=42244674

Family Applications (2)

Application Number Title Priority Date Filing Date
EP10158923A Withdrawn EP2374910A1 (fr) 2010-04-01 2010-04-01 Acier, produit plat en acier, composant en acier et procédé de fabrication d'un composant en acier
EP11711594.9A Active EP2553133B1 (fr) 2010-04-01 2011-04-01 Acier, produit plat en acier, élément en acier et procédé de fabrication d'un élément en acier

Family Applications Before (1)

Application Number Title Priority Date Filing Date
EP10158923A Withdrawn EP2374910A1 (fr) 2010-04-01 2010-04-01 Acier, produit plat en acier, composant en acier et procédé de fabrication d'un composant en acier

Country Status (12)

Country Link
US (1) US20120279621A1 (fr)
EP (2) EP2374910A1 (fr)
JP (1) JP5871901B2 (fr)
KR (1) KR20130014520A (fr)
CA (1) CA2780082A1 (fr)
DK (1) DK2553133T3 (fr)
ES (1) ES2524352T3 (fr)
MX (1) MX2012007359A (fr)
PL (1) PL2553133T3 (fr)
PT (1) PT2553133E (fr)
UA (1) UA108091C2 (fr)
WO (1) WO2011121118A2 (fr)

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RU2599934C2 (ru) 2012-08-15 2016-10-20 Ниппон Стил Энд Сумитомо Метал Корпорейшн Стальной лист для горячей штамповки, способ его изготовления и изделие из горячештампованного стального листа
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EP2754603B1 (fr) * 2013-01-10 2017-07-19 Volvo Car Corporation Procédé, renforcement de véhicule et véhicule
EP2886332B1 (fr) 2013-12-20 2018-11-21 ThyssenKrupp Steel Europe AG Produit en acier plat, et procédé de fabrication d'un composant d'une carrosserie de véhicule automobile et d'une carrosserie de véhicule automobile.
CN105829561B (zh) 2013-12-27 2019-06-28 日本制铁株式会社 热压钢板构件、其制造方法以及热压用钢板
JPWO2015097891A1 (ja) 2013-12-27 2017-03-23 新日鐵住金株式会社 熱間プレス鋼板部材、その製造方法及び熱間プレス用鋼板
DE102014001979A1 (de) * 2014-02-17 2015-08-20 Wisco Tailored Blanks Gmbh Verfahren zum Laserschweißen eines oder mehrerer Werkstücke aus härtbarem Stahl im Stumpfstoß
CN104404367B (zh) * 2014-12-10 2016-08-31 东北大学 一种高强度高塑性冷轧低碳钢及其制备方法
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JP7215518B2 (ja) * 2020-05-15 2023-01-31 Ｊｆｅスチール株式会社 熱間プレス部材およびその製造方法
KR20220071545A (ko) 2020-11-24 2022-05-31 현대자동차주식회사 Twb 공법을 이용한 핫스탬핑 성형체 및 그 제조방법
CN118302546A (zh) 2021-08-19 2024-07-05 蒂森克虏伯钢铁欧洲股份公司 用于在高温下成型的、具有改进加工特性的钢材
WO2023020932A1 (fr) 2021-08-19 2023-02-23 Thyssenkrupp Steel Europe Ag Acier doté de propriétés de traitement améliorées pour le travail à des températures élevées
EP4324950A1 (fr) 2022-08-18 2024-02-21 ThyssenKrupp Steel Europe AG Acier ayant des propriétés améliorées d'usinage destiné au formage à des températures élevées
WO2024149909A1 (fr) 2023-02-17 2024-07-18 Thyssenkrupp Steel Europe Ag Acier à haute résistance à la traction ayant une résistance améliorée à la fragilisation par l'hydrogène
EP4460586B1 (fr) 2023-02-17 2025-08-13 ThyssenKrupp Steel Europe AG Acier à haute résistance présentant une résistance améliorée à la fragilisation par l'hydrogène
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EP2553133B1 (fr) 2014-08-27
WO2011121118A2 (fr) 2011-10-06
CA2780082A1 (fr) 2011-10-06
MX2012007359A (es) 2012-08-01
WO2011121118A3 (fr) 2012-02-02
EP2374910A1 (fr) 2011-10-12
PL2553133T3 (pl) 2015-03-31
ES2524352T3 (es) 2014-12-05
UA108091C2 (uk) 2015-03-25
PT2553133E (pt) 2014-11-27
KR20130014520A (ko) 2013-02-07
JP2013527312A (ja) 2013-06-27
US20120279621A1 (en) 2012-11-08
JP5871901B2 (ja) 2016-03-01

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