EP2297367A1 - Procédé de production d'une pièce moulée en acier à structure à prédominance ferritique-bainitique - Google Patents

Procédé de production d'une pièce moulée en acier à structure à prédominance ferritique-bainitique

Info

Publication number
EP2297367A1
EP2297367A1 EP09741994A EP09741994A EP2297367A1 EP 2297367 A1 EP2297367 A1 EP 2297367A1 EP 09741994 A EP09741994 A EP 09741994A EP 09741994 A EP09741994 A EP 09741994A EP 2297367 A1 EP2297367 A1 EP 2297367A1
Authority
EP
European Patent Office
Prior art keywords
max
steel
temperature
time
bainitization
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
EP09741994A
Other languages
German (de)
English (en)
Other versions
EP2297367B9 (fr
EP2297367B1 (fr
Inventor
Jian Bian
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
Publication of EP2297367A1 publication Critical patent/EP2297367A1/fr
Application granted granted Critical
Publication of EP2297367B1 publication Critical patent/EP2297367B1/fr
Publication of EP2297367B9 publication Critical patent/EP2297367B9/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

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
    • 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
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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
    • 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
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • 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
    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • 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

Definitions

  • DJ e invention relates to a method for producing a steel molding with a predominantly ferritic-bainitic Gefuge.
  • hot-press molded components produced from high-strength steel are nowadays used in those areas of the body which may be exposed to particularly high loads in the event of a crash .
  • Examples of such steel moldings are the A and B pillars, called the Stoßfanger and Turaufpralltrager a passenger car.
  • the sheet metal blanks concerned are heated to a generally above the Austenitmaschinestemperatur of the respective steel deformation temperature and placed in the heated state in the tool of a forming press.
  • the sheet metal blank or the component formed from it experience a contact with the cool tool rapid cooling, which results in hardened components in the component. It may be sufficient if the component cools without aktxve cooling only by the contact with the tool. However, rapid cooling can also be supported by the fact that the tool itself is actively cooled.
  • Em steel comparable to steel 22MnB5 is known from JP 2006104526A.
  • This known steel contains in addition to Fe and unavoidable impurities (xn wt .-%) 0.05 - 0.55% C, max. 2% Si, 0.1-3% Mn, max. 0.1% P and max. 0.03% S.
  • additional amounts of 0.0002 - 0.005% B and 0.001 - 0.1% Ti can be added to the steel.
  • the respective Ti content serves to bind the nitrogen present in the steel. In this way, the boron present in the steel can develop its strength-increasing effect as completely as possible.
  • sheets made of the composite steel in this way are first produced be preheated 950 0 C, lying temperature - then to an above the AEC 3 temperature, typically in the range of 850th During the subsequent rapid cooling in the pressing tool, starting from this temperature range, the martensitic joint, which ensures the desired high strength, is formed in the component molded from the respective sheet metal blank. It has a favorable effect that the sheet metal parts heated to the stated temperature level can be formed into complex shaped components at relatively low forming forces. This is especially true for such sheet metal parts, which are made of high-strength steel and provided with a corrosion protection coating.
  • the components produced from boron-alloyed steels in the above-described manner achieve strengths of more than 1,500 MPa.
  • the required complete martensitic structure of the components has the result that the components have an insufficient residual elongation at break of 5-6% for many applications.
  • the relatively low residual elongation at break is associated with a low toughness. In the case of applications in which good deformation behavior is required in the event of a crash, this leads to components made of boron-alloyed steel in the known manner frequently no longer meeting these requirements. This applies in particular when the components to be produced are parts for an automobile body.
  • a board or a preformed mold component each consisting of a steel of the above type, heated in a heating device to an austenitizing and then fed via a transport path to a hardening process.
  • transport portions of the first type of board or of the molded component which are intended to have higher ductility properties in the final component, are quenched from a predetermined cooling start temperature which is above the ⁇ - ⁇ transformation temperature. This quenching is terminated when a predetermined cooling stop temperature is reached, before conversion to ferrite and / or pearlite has taken place or after a slight conversion in ferrite and / or perlite.
  • the board or the respective molded part is held isothermally to convert the austenite into ferrite and / or perlite.
  • the tempering temperature of the areas of the second kind which should have relatively lower ductile properties in the final component, is kept just high enough for sufficient martensite formation to take place in the areas of the second type during a hardening process.
  • the cooling is carried out.
  • the resulting molded part is immersed in a separate operation in a quenching tank or the like to form the desired martensitic Hartegefuge.
  • This procedure also requires a Prozeßbowung that can be incorporated only with great effort in a modern production plant.
  • there is also the problem with the components produced by this known method that while they have a high strength, they are at the same time so brittle that they do not meet the requirements for their deformability which are set in practice.
  • the object of the invention was to provide a method with which it is possible to produce in a process-technically simple manner Stahlformtei Ie in which a high strength is combined with a good residual elongation at break.
  • a steel shaped part is produced with a predominantly ferritic-Bavarian mesh.
  • a starting material in the form of a steel plate or a preformed steel part is provided. If a hitherto undeformed steel plate is processed as a starting material, the entire process is referred to as a "one-step" process. If, on the other hand, a preformed steel part is processed, this is referred to as a two-stage process, whereby in the first stage a previously undeformed blank is deformed so that the steel component thus obtained has not yet reached its final shape.
  • the respective starting material consists of a steel of a known composition which, in addition to iron and unavoidable production-related impurities (in% by weight) C: 0.02-0.6%, Mn: 0.5-2.0%, Al : 0.01 - 0.06%, Si: up to 0.4%, Cr: up to 1.2%, P: up to 0.035%, S: up to 0.035% and optionally one or more elements from the group "Ti, B, Mo, Ni, Cu, N", wherein - if present - Ti in a content of up to 0.05%, Cu in a content of up to 0.01%, B in contents of 0 , 0008 - 0.005%, Mo in contents of up to 0.3%, Ni in contents of up to 0.4%, N m contents of up to 0.01%.
  • the as-assembled starting material (steel plate or preformed steel part) is soaked through at a heating temperature lying between the AcI and the Ac3 temperature of the steel such that incomplete austenitisation of the starting material occurs. Accordingly, at the end of the austenitizing phase, the microstructure of the starting material consists of ferrite and austenite.
  • Vormate ⁇ al is placed in a press mold and molded therein to the steel molding. Press-hardening takes place in a temperature range in which the microstructure of the primary material in the two-phase region is composed of ferrite and austenite.
  • the steel mold part according to the invention is kept substantially isothermally on the Bainit Siegstemperatur over a bainitization time until a Gefuge has set in the steel mold part, the majority of ferrite and bainite exists.
  • the bainitization temperature to be set in each case depends on the bainite transformation temperature, which is differentiated upward in each case according to the chemical composition of the enriched austenite by the martensite start temperature and perlite transition temperature.
  • Press hardening is significantly influenced by the austenitizing and mold temperature. This must be so fast that the board is cooled without conversion to the Bainitumwandlungstemperatur and kept constant at this temperature.
  • a Gefuge which has in addition to the ferritic and Bavarian constituent parts minor amounts of retained austenite and possibly below 5% levels of martensite.
  • the residual austenite contents in the resulting component which are essentially determined by the carbon content, can be up to 10%.
  • the steel mold is cooled to room temperature.
  • the temperature control is controlled with respect to the austenitizing process and the subsequent press-hardening in such a way that a mixture of ferrite, bainite and a proportion of retained austenite in the component is established.
  • the erfmdungsgelaute method thus provides a steel component whose Gefuge is characterized by a fer ⁇ tisch-bainitician microstructure.
  • This bainitic microstructure gives a component produced erfxndungsgeINE improved Verformungsei properties, in particular an improved residual elongation at break.
  • steel moldings produced according to the invention have an improved crash behavior, without the need for separate tempering treatment, since bainite can be regarded as a type of tempered martensite.
  • the erfmdungsge64e method allows the steel component to cool more slowly than in the conventional method in which the cooling takes place in the tool with the aim to produce martensitic Hartegefuge. Therefore, in a erfI ndungsgedorfen process, the risk of the formation of component distortion is minimized and the components produced according to the invention are characterized by a particularly high dimensional stability.
  • the pressing tool can also be specifically heated to carry out the method according to the invention.
  • the ferrite and Baimtanteile should be in the Gefuge of the steel molding at the end of Bainitmaschineszeit Jn sum at least 90%, the ferrite and bainite each should be at least 30%.
  • the curing according to the invention is prevented as completely as possible, it is fundamentally advantageous if, at the end of the bainitization time, the martensite portion of the steel molding is less than 1%, in particular limited to tracks.
  • the alloy of the steel from which the starting material to be processed according to the invention is conventional
  • tempered steel has in addition to iron and unavoidable impurities (in wt .-%) C:
  • MnB steels which are suitable for the process according to the invention have C: 0.25-0.6
  • the austenitizing temperature of the steels which is made of processed accordance with the invention starting material, in the range 750-810 0 C.
  • the intended for the fürerwarmen at the warming temperature heating time is typically in the range 6 - 15 minutes.
  • the starting material is provided with a corrosion-protecting metallic coating.
  • This coating also protects the respective starting material (steel plate, preformed steel part) from the press mold during transport from the oven, in which it is preheated to the austenitizing temperature.
  • the corrosion protection coating can be designed so that it protects an oxidation of the hot steel substrate with the ambient oxygen even when transported in air.
  • a particularly practical variant of the method according to the invention is characterized in that the press forming and the bainitization of the steel component produced in the course of the press forming takes place in the press forming tool.
  • a particularly advantageous variant of the invention provides that after the compression molding of the starting material, the steel mold part then obtained remains in the compression mold and brought there to the Bamit avoirstemperatur and kept for the Bamitmaschineszeit.
  • the press mold is preferably tempered so that the starting material, starting from one above the Bainitisi tion temperature lying temperature during their compression deformation to the steel component to the Ba Lnitmaschinestemperatur be cooled.
  • the tool closing time of the pressing tool, within which the shaping, Abkluhlung and Bainitmaschine of the steel molding takes place in this case is usually 5 - 60 seconds, especially 20 - 60 seconds.
  • the typical range of the bainitization temperature at which the baintization according to the invention with the aim of Formation of a ferritic / bainitic Gefuges is preferably carried out, is typically bounded below by the martensite [respective steel composition of the raw material, while it may be adjusted upwardly in each case lower than 500 0 C in order to avoid the formation of pearlite.
  • steel blanks which have been divided off from a hot-rolled or cold-rolled flat product such as strip or sheet, are suitable. It is likewise possible to apply the method according to the invention to a steel part which has been preformed in a previous work step. The latter is useful, for example, when the shape of the steel component to be produced is so complex that several shaping steps are required for its production.
  • steel components produced according to the invention are particularly suitable for use as crash-relevant parts of an automobile body.
  • the inventive method is particularly suitable for the production of Longitudinal and bottom crossbeams, which in practice should have a particularly good energy absorption capacity.
  • FIG. 1 shows a typical course of the temperature T over the time t, which is maintained during the execution of a method according to the invention. Accordingly, as a starting material to be deformed in each case to a steel component, for example, provided with a corrosion-protective AlSi coating steel plate first heated to an austenitizing TA, which is below the Ac3 temperature but above the AcI temperature of the steel, from which the steel plate respectively is made. In the case of this
  • Austenitizing temperature TA the Stahlplatme is held for a time tA until the steel plate is completely soaked through, so that there is an existing austenite and ferrite Mischgefuge.
  • a in Fig. 1 The area where the steel has a groove is indicated by A in Fig. 1, while the area of the mixed ferrite and austenite core is indicated by "A + F”.
  • the steel plate After the end of the austenitizing time tA, the steel plate is transported to a press forming tool.
  • the transfer time required until the mold is closed is designated tT in FIG.
  • the temperature TW at which the steel plate enters the die is still within the temperature range Ac3 - AcI.
  • the press mold is equipped with a tempering device, which keeps it at a constant temperature, which corresponds to the Ba mitleitersstemperatur TB.
  • the shaped steel part formed from the steel plate and coming into direct contact with the press mold is accordingly cooled to the bainitizing temperature TB over a cooling time tK.
  • the bainitization temperature TB is above the martensite start temperature Ms but below the pearlite transformation temperature.
  • M m Fig. 1 marked with P.
  • F indicates the area where pure ferrite is present and M denotes the area in which martensite is present.
  • the steel component still sitting in the die is kept isothermal at the bainitizing temperature TB for a period of time tB.
  • the Baimtleiterszeit tB is dimensioned so that at its end the Gefuge of the steel component is substantially completely baimtisch.
  • the cooling of the steel plate in the tempered pressing tool takes place within the cooling time tK so fast that the steel passes through the two-phase mixing area A + F and conversion in the martensite area M and perlite area P is prevented, wherein the martensite formation is avoided as completely as possible.
  • the tool closing time tW which comprises the cooling time tK and the bainitization time tB, is 5 to 60 seconds, depending on the complexity of the shape of the steel component to be produced and the sheet thickness of the respectively processed steel plate.
  • the first steel plate SPl has been heated to an austenitizing temperature TA of 780 0 C and maintained at this temperature TA for a Austenitmaschineszeit tA of 6 min.
  • the steel plate SPI has been transported in a 6 to 12 s transfer time tT in air in a press mold, which has been heated to a bainitization temperature TB of 400 0 C and kept constant at this temperature TB.
  • Pressing tool has been press-formed over a tool closing time tW of 40 s.
  • the total press temperature t comprised the cooling time IK in which the steel plates SPl had been cooled from the tool inlet temperature TW to the Bamitis release temperature TB, and the bittitization time tB in which the bamit fusion was formed in the steel component hot-press-forged in the press forming tool.
  • the pressing tool has been opened and the steel component has been cooled to room temperature in still air.
  • the Gefuge of the thus obtained steel molding had a Fer ⁇ tantei] of 50%, a Baimtanteil of 40%, a Restauustemtanteil of 6% and a Martensitanteil of 4%.
  • the inventive baini tables press hardening is thus a process for hot pressing, in which instead of the usually produced Martensitgefuges a predominantly consisting of ferrite and bainite Gefuge is set by an isothermal conversion during press-hardening on each press-formed steel component.
  • the resulting ferritic / bainitic structure has improved residual elongation at high strength compared to martensite.

Abstract

L'objectif de l'invention est de produire, à l'aide de techniques de processus simples, des pièces moulées en acier présentant une résistance élevée et un bon allongment résiduel à la rupture. A cette fin, un matériau de départ en acier est préparé, qui contient (en pourcentages en poids): C: 0,02 à 0,6 %, Mn: 0,5 à 2,0 %, Al: 0,01 à 0,06 %, Si : 0,4 % max, Cr: 1,2 % max, P: 0,035 % max, S: 0,035 % max, ainsi qu'éventuellement un ou plusieurs éléments du groupe comprenant: Ti, Cu, B, Mo, Ni et N, à condition que: Ti: 0,05 % max, Cu: 0,01 % max, B: 0,0008 à 0,005 %, Mo: 0,3 % max, Ni: 0,4 % max, et N: 0,01 % max, le reste étant du fer et des impuretés inévitables. Le matériau de départ est chauffé à coeur à une température d'échauffement (TA) comprise entre la température Ac1 et la température Ac3, de sorte à produire une austénisation éventuellement partielle dudit matériau; puis il est placé dans une matrice de compression où il est moulé pour former la pièce moulée en acier. La pièce moulée en acier est ensuite amenée à une température de formation de bainite (TB) qui est supérieure à la température de départ de formation de martensite (Ms), et inférieure à la température de transformation en perlite de l'acier à partir duquel le matériau de départ est produit. Après le refroidissement, la pièce moulée en acier est maintenue, pendant une période de bainitisation (tB), de manière sensiblement isotherme à une température de formation de bainite (TB), jusqu'à obtention, dans la pièce moulée en acier, d'une structure principalement constituée de ferrite et de bainite, dont la teneur en martensite est inférieure à 5%, des teneurs en austénite résiduelle inférieures ou égales à 10 % pouvant être présentes. Une fois la période de bainitisation (tB) terminée, la pièce moulée en acier est amenée à température ambiante.
EP09741994.9A 2008-05-06 2009-04-24 Procédé de production d'une pièce moulée en acier à structure à prédominance ferritique-bainitique Active EP2297367B9 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102008022399A DE102008022399A1 (de) 2008-05-06 2008-05-06 Verfahren zum Herstellen eines Stahlformteils mit einem überwiegend ferritisch-bainitischen Gefüge
PCT/EP2009/054961 WO2009135776A1 (fr) 2008-05-06 2009-04-24 Procédé de production d'une pièce moulée en acier à structure à prédominance ferritique-bainitique

Publications (3)

Publication Number Publication Date
EP2297367A1 true EP2297367A1 (fr) 2011-03-23
EP2297367B1 EP2297367B1 (fr) 2017-06-07
EP2297367B9 EP2297367B9 (fr) 2017-09-13

Family

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Application Number Title Priority Date Filing Date
EP09741994.9A Active EP2297367B9 (fr) 2008-05-06 2009-04-24 Procédé de production d'une pièce moulée en acier à structure à prédominance ferritique-bainitique

Country Status (5)

Country Link
US (1) US8888934B2 (fr)
EP (1) EP2297367B9 (fr)
CA (1) CA2725210C (fr)
DE (1) DE102008022399A1 (fr)
WO (1) WO2009135776A1 (fr)

Families Citing this family (20)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102009056443A1 (de) * 2009-12-02 2011-06-09 Benteler Automobiltechnik Gmbh Crashbox und Verfahren zu deren Herstellung
DE102010012830B4 (de) 2010-03-25 2017-06-08 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung einer Kraftfahrzeugkomponente und Karosseriebauteil
DE102010048209C5 (de) * 2010-10-15 2016-05-25 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung eines warmumgeformten pressgehärteten Metallbauteils
KR101033767B1 (ko) * 2010-11-03 2011-05-09 현대하이스코 주식회사 열처리 경화 강판을 이용한 국부적으로 이종강도를 가지는 자동차 부품 제조방법
EP2719786B1 (fr) * 2011-06-10 2016-09-14 Kabushiki Kaisha Kobe Seiko Sho Article moulé par pressage à chaud, procédé pour produire celui-ci, et tôle d'acier mince pour moulage à la presse à chaud
DE102012024626A1 (de) 2012-12-17 2014-06-18 GM Global Technology Operations LLC (n. d. Gesetzen des Staates Delaware) Fahrzeugkarosserie und Verfahren zur Fertigung eines Formteils dafür
CN104195455B (zh) * 2014-08-19 2016-03-02 中国科学院金属研究所 一种基于碳配分原理的热冲压烘烤韧化钢及其加工方法
CN104498830B (zh) * 2014-12-30 2017-06-23 南阳汉冶特钢有限公司 一种合金结构钢及其生产方法
WO2017098302A1 (fr) * 2015-12-09 2017-06-15 Arcelormittal Structure de soubassement de carrosserie de véhicule comportant un élément de renfort entre une poutre longitudinale et une partie de bas de caisse côté inférieur
US10385415B2 (en) 2016-04-28 2019-08-20 GM Global Technology Operations LLC Zinc-coated hot formed high strength steel part with through-thickness gradient microstructure
US10619223B2 (en) 2016-04-28 2020-04-14 GM Global Technology Operations LLC Zinc-coated hot formed steel component with tailored property
CN106676405A (zh) * 2016-12-09 2017-05-17 天长市天龙泵阀成套设备厂 高强度合金钢
CN106756512B (zh) * 2017-01-12 2018-12-18 唐山钢铁集团有限责任公司 一钢多级的热轧复相高强钢板及其生产方法
WO2019222950A1 (fr) 2018-05-24 2019-11-28 GM Global Technology Operations LLC Procédé pour améliorer à la fois la résistance et la ductilité d'un acier trempé sur presse
CN112534078A (zh) 2018-06-19 2021-03-19 通用汽车环球科技运作有限责任公司 具有增强的机械性质的低密度压制硬化钢
US11530469B2 (en) 2019-07-02 2022-12-20 GM Global Technology Operations LLC Press hardened steel with surface layered homogenous oxide after hot forming
WO2021009543A1 (fr) * 2019-07-16 2021-01-21 Arcelormittal Procédé de production de pièce en acier et pièce en acier
CN110527914A (zh) * 2019-09-25 2019-12-03 唐山汇丰钢铁有限公司 一种建筑拉条专用钢及其生产工艺
CA3177824A1 (fr) * 2020-05-18 2021-11-25 Timothy W. Skszek Procede pour le traitement d'un acier a haute resistance avance
CN114959422A (zh) * 2022-06-06 2022-08-30 山东冀凯装备制造有限公司 一种高强度低合金贝氏体铸钢的制备方法

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4426235A (en) * 1981-01-26 1984-01-17 Kabushiki Kaisha Kobe Seiko Sho Cold-rolled high strength steel plate with composite steel structure of high r-value and method for producing same
FR2780984B1 (fr) 1998-07-09 2001-06-22 Lorraine Laminage Tole d'acier laminee a chaud et a froid revetue et comportant une tres haute resistance apres traitement thermique
DE10208216C1 (de) 2002-02-26 2003-03-27 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung eines metallischen Bauteils
JP4975245B2 (ja) 2004-10-06 2012-07-11 新日本製鐵株式会社 高強度部品の製造方法
EP1767659A1 (fr) * 2005-09-21 2007-03-28 ARCELOR France Procédé de fabrication d'une pièce en acier de microstructure multi-phasée
DE102005054847B3 (de) 2005-11-15 2007-10-04 Benteler Automobiltechnik Gmbh Hochfestes Stahlbauteil mit gezielter Deformation im Crashfall
DE102006019395A1 (de) * 2006-04-24 2007-10-25 Thyssenkrupp Steel Ag Vorrichtung und Verfahren zum Umformen von Platinen aus höher- und höchstfesten Stählen
DE102006053819A1 (de) 2006-11-14 2008-05-15 Thyssenkrupp Steel Ag Verfahren zum Herstellen eines Bauteil durch Warmpresshärten und hochfestes Bauteil mit verbesserter Bruchdehnung

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO2009135776A1 *

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EP2297367B9 (fr) 2017-09-13
US8888934B2 (en) 2014-11-18
CA2725210A1 (fr) 2009-11-12
CA2725210C (fr) 2016-05-31
WO2009135776A1 (fr) 2009-11-12
US20110132502A1 (en) 2011-06-09
EP2297367B1 (fr) 2017-06-07
DE102008022399A1 (de) 2009-11-19

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