EP2683839B1 - Procédé pour produire un acier formable à haute résistance et acier formable à haute résistance produit par celui-ci - Google Patents

Procédé pour produire un acier formable à haute résistance et acier formable à haute résistance produit par celui-ci Download PDF

Info

Publication number
EP2683839B1
EP2683839B1 EP12708008.3A EP12708008A EP2683839B1 EP 2683839 B1 EP2683839 B1 EP 2683839B1 EP 12708008 A EP12708008 A EP 12708008A EP 2683839 B1 EP2683839 B1 EP 2683839B1
Authority
EP
European Patent Office
Prior art keywords
strip
martensite
temperature
austenite
carbon
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.)
Revoked
Application number
EP12708008.3A
Other languages
German (de)
English (en)
Other versions
EP2683839A1 (fr
Inventor
David Neal Hanlon
Stefanus Matheus Cornelis VAN BOHEMEN
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.)
Tata Steel Nederland Technology BV
Original Assignee
Tata Steel Nederland Technology BV
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
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=44279692&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP2683839(B1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by Tata Steel Nederland Technology BV filed Critical Tata Steel Nederland Technology BV
Priority to EP12708008.3A priority Critical patent/EP2683839B1/fr
Publication of EP2683839A1 publication Critical patent/EP2683839A1/fr
Application granted granted Critical
Publication of EP2683839B1 publication Critical patent/EP2683839B1/fr
Revoked legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

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
    • 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
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • 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
    • 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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment

Definitions

  • WO2010/029983 discloses a method for manufacturing a high-strength steel sheet, comprising hot-rolling and then cold-rolling a billet to be formed into a steel sheet having the composition on a mass percent basis: 0.17%-0.73% C; 3.0% or less Si; 0.5%-3.0% Mn; 0.1% or less P; 0.07% or less S; 3.0% or less Al; 0.010% or less N, balance Fe and incidental impurities to form a cold-rolled steel sheet, annealing the cold-rolled steel sheet in an austenite single-phase region for 15 seconds to 600 seconds, cooling the cold-rolled steel sheet to a first temperature range of 50 °C to 300 °C at an average cooling rate of 8 °C/s or more, heating the cold-rolled steel sheet to a second temperature range of 350 °C to 490 °C, and maintaining the cold-rolled steel sheet at the second temperature range for 5 seconds to 1000 seconds.
  • austenite is simply chemically stabilised by large additions of Mn. Although clearly differentiated strength-ductility combinations can be achieved in this way, processing has proven to be difficult since hard, brittle martensitic phases are developed in intermediate product. This renders further processing, such as cold rolling, difficult at dimensions relevant to commercial processing. Furthermore, alloy costs are high due to the high manganese content.
  • the steel is then subjected to a thermal treatment to partition carbon from the martensite into the austenite.
  • the carbon enrichment of the austenite fraction is achieved by partitioning from martensite or low temperature bainitic transformation or preferably a combination of both. By this partitioning, the formation of carbides is suppressed and the austenite is stabilised rather than decomposed.
  • Combined stabilisation with partitioning and bainitic transformation enables the amount of austenite and the microstructure in which it is embedded to be optimised.
  • the bainitic transformation also leads to carbon enrichment of the remaining austenite because the formation of carbides is suppressed. All compositions are given in weight percentages, unless otherwise indicated.
  • the final microstructure of the steel comprises martensite, bainite and carbon-enriched austenite and, if T 1 ⁇ Ac 3 , equiaxed ferrite.
  • the stabilisation of austenite results in the steel exhibiting improved ductility relative to traditional high strength steels.
  • V Vanadium
  • C Vanadium
  • N Vanadium
  • V addition up to 0.4wt% is effective. Higher additions are undesirable for reasons of cost and because excessive levels of precipitation tie up high amounts of C. Since free C is required for austenite stabilisation too high V requires increased C addition.
  • V is below 0.1%.
  • the equilibrium transformation temperature Ae 3 is only determined by the composition, the value of the corresponding Ac 3 temperature is not a constant value as its value depends among others on the heating rate during which Ac 3 is measured and the starting microstructure of the steel. Usually Ac 3 is determined using dilatometry. When the heating rate used during dilatometry and the microstructure of the test specimen are those used in the process according to the invention, the value of Ac 3 is easy to determine.
  • the correct balance of isothermal holding temperature and isothermal holding time must be chosen for each composition. These can be determined by means of dilatometry as described hereinbelow.
  • the partitioning temperature and time are chosen such as to optimise the enrichment of carbon in the austenite but without creation of deleterious microstructures during the isothermal hold.
  • the strip is cooled to ambient temperature.
  • the strip may also be coated with zinc or other such metallic layers using a suitable method of deposition either in-line or in a following process step.
  • Si is preferred to that of Al such that a minimum silicon content of 1wt% and a max maximum aluminium content of 0.5 wt% is defined.
  • Si provides substantial strengthening allowing the achievement of ultra high strength, more effectively suppresses carbide formation enabling longer isothermal holds without formation of large volumes of coarse iron carbides, and because it does not accelerate bainite formation to the same extent as Al thus preventing excessive formation of bainite and enabling higher strengths to be achieved.
  • the metal or metal alloy coating is zinc, aluminium, magnesium or alloys thereof.
  • the steel is afforded sacrificial corrosion protection since the zinc and aluminium will oxidise in preference to iron in the steel.
  • the metallic coating is provided by hot-dip galvanising or by electro-galvanising.
  • the partitioning step for 20s at 330°C shows no dilation of the sample, which means that no bainite is formed, carbon is partitioned and the martensite is only marginally tempered.
  • the transformation to martensite re-starts at temperatures lower than the quench temperature of 280°C, namely at 250°C, which indicates that the austenite has been stabilized due to carbon partitioning.
  • Increased partition times at 330°C show that the transformation to martensite re-starts at lower temperatures than 250°C.
  • the dilation observed during annealing of the sample for 20s at 440°C means that bainite is formed.
  • carbon is partitioned and the martensite is tempered. The consequence of this high partitioning temperature is that the martensite is severely tempered.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Claims (14)

  1. Procédé de production d'un acier trempé et partitionné en utilisant une bande d'acier laminée à froid et recuite contenant (en % en poids) :
    • 0,18 - 0,4 % C
    • 1,5 - 4,0 % Mn
    • 0,5 - 2,0 % Si
    • 0 - 1,5 % Al
    • 0 - 0,5 % Mo
    • 0 - 0,5% Ti
    • 0 - 0,1 % V
    • 0 - 0,010 % Nb
    • 0 - 0,005 % B
    • 0 - 0,015 % N
    • 0 - 0,08 % P
    • 0-0,01 %S
    • 0 - 0,06 % Sb
    • 0 - 0,05 % Ca
    • 0 - 0,5 % Cr
    • 0-1,0% Ni
    • le reste étant du fer et des impuretés inévitables
    dans lequel le procédé de recuit comprend les étapes suivantes :
    (i) réchauffer la bande laminée à froid à une température de recuit T1 comprise entre Ac3-40 et Ac3+80 ;
    (ii) maintenir la bande à T1 pendant un temps de recuit t1 compris entre 10 et 200 secondes ;
    (iii) refroidir la bande recuite à la vitesse de refroidissement critique CR1 pour éviter la formation de ferrite et de perlite à une température de trempe T2 pour produire une microstructure dans la bande comprenant une fraction de martensite et une fraction d'austénite résiduelle ;
    (iv) recuire pour repartitionnement la bande refroidie à une température T3 pour enrichir l'austénite en carbone en repartitionnant le carbone à partir de la martensite à la fraction d'austénite pendant un temps de repartitionnement t2 compris entre 20 et 500 secondes, dans lequel la fraction de martensite est comprise entre 60 et 90 % de la microstructure au début du recuit de repartitionnement dans lequel (Ms-70) < T3 ≤ (Ms+50) ;
    (v) refroidir la bande à une vitesse de refroidissement CR2 à température ambiante.
  2. Procédé selon la revendication 1, dans lequel CR1 est d'au moins 30 °C/s.
  3. Procédé selon la revendication 1 ou 2, dans lequel la fraction de martensite est au maximum de 85 % de la microstructure au début du recuit de partitionnement.
  4. Procédé selon l'une quelconque des revendications précédentes, dans lequel : AC 3 - 40 < T 1 ≤ AC 3 + 50 pour le carbone entre 0 , 18 - 0 , 3 % C
    Figure imgb0014
    ou AC 3 - 20 < T 1 ≤ AC 3 + 30 pour le carbone entre 0 , 3 à 0 , 4 % C
    Figure imgb0015
  5. Procédé selon l'une quelconque des revendications précédentes, dans lequel T1 est supérieure à Ac3.
  6. Procédé selon l'une quelconque des revendications précédentes, dans lequel la bande laminée à froid contient au maximum 0,5 % d'Al.
  7. Procédé selon l'une quelconque des revendications précédentes, dans lequel la bande laminée à froid contient au moins 0,25 % de C et au moins 0,01 % d'Al.
  8. Procédé selon l'une quelconque des revendications précédentes, dans lequel T2 est égale à T3.
  9. Procédé selon l'une quelconque des revendications 1 à 7 dans lequel T2 est inférieure à T3.
  10. Procédé selon l'une quelconque des revendications précédentes, dans lequel la bande laminée à froid et recuite est revêtue d'une ou plusieurs couche(s) métallique(s), de préférence dans lequel l'étape de fourniture de revêtement métallique est par galvanisation à chaud ou électro-galvanisation.
  11. Bande d'acier produite par l'une quelconque des revendications 1 à 10, dans laquelle l'acier a une microstructure contenant au moins 5 % d'austénite, dans laquelle la microstructure contient de 60 à 90 % (en volume) de martensite traitée thermiquement et dans laquelle un e-rapport est d'au moins 1,8 et une résistance à la traction (UTS) d'au moins 900 MPa, dans laquelle l'e-rapport est défini comme emeasured/ecalculated et dans laquelle ecalculated est calculé selon : e calculated = k ⁢ 1 UTS 3
    Figure imgb0016
    et dans laquelle emeasured est l'allongement mesuré à partir d'un échantillon de longueur de calibre de 80 mm à 1 mm d'épaisseur, ou dans laquelle emeasured est l'allongement mesuré à une autre géométrie et converti en un allongement équivalent sur un calibre de 80 mm à 1 mm d'épaisseur à l'aide de : e 2 = e 1 L 1 L 2 • A 2 A 1 m
    Figure imgb0017
  12. Bande d'acier selon la revendication 11, dans laquelle la microstructure contient en outre un ou plusieurs parmi la bainite, la martensite, la martensite trempée, la ferrite, les carbures fins.
  13. Bande d'acier selon la revendication 11 ou 12, dans laquelle la microstructure ne contient pas de ferrite et/ou de cémentite grossière.
  14. Bande d'acier selon l'une quelconque des revendications 11 à 13, dans laquelle le rapport limite d'élasticité/résistance à la traction est d'au moins 0,6.
EP12708008.3A 2011-03-07 2012-03-07 Procédé pour produire un acier formable à haute résistance et acier formable à haute résistance produit par celui-ci Revoked EP2683839B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP12708008.3A EP2683839B1 (fr) 2011-03-07 2012-03-07 Procédé pour produire un acier formable à haute résistance et acier formable à haute résistance produit par celui-ci

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
EP11157239 2011-03-07
EP12708008.3A EP2683839B1 (fr) 2011-03-07 2012-03-07 Procédé pour produire un acier formable à haute résistance et acier formable à haute résistance produit par celui-ci
PCT/EP2012/053856 WO2012120020A1 (fr) 2011-03-07 2012-03-07 Procédé pour produire un acier formable à haute résistance et acier formable à haute résistance produit par celui-ci

Publications (2)

Publication Number Publication Date
EP2683839A1 EP2683839A1 (fr) 2014-01-15
EP2683839B1 true EP2683839B1 (fr) 2015-04-01

Family

ID=44279692

Family Applications (1)

Application Number Title Priority Date Filing Date
EP12708008.3A Revoked EP2683839B1 (fr) 2011-03-07 2012-03-07 Procédé pour produire un acier formable à haute résistance et acier formable à haute résistance produit par celui-ci

Country Status (3)

Country Link
EP (1) EP2683839B1 (fr)
ES (1) ES2535420T3 (fr)
WO (1) WO2012120020A1 (fr)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106244924A (zh) * 2016-08-31 2016-12-21 东北大学 一种冷轧淬火延性钢及制备方法
US11136656B2 (en) 2015-05-21 2021-10-05 Cleveland-Cliffs Steel Properties Inc. High manganese 3rd generation advanced high strength steels
EP3899067B1 (fr) * 2018-12-18 2023-09-13 ArcelorMittal Tôle d'acier laminée à froid traitée thermiquement et son procédé de fabrication
WO2023170245A1 (fr) * 2022-03-10 2023-09-14 Tata Steel Nederland Technology B.V. Tôle d'acier à haute résistance présentant une excellente extensibilité de trou et son procédé de production
EP3175005B1 (fr) * 2014-07-30 2024-03-20 ArcelorMittal Procédé de fabrication d'une pièce en acier à haute résistance

Families Citing this family (38)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103160680A (zh) * 2013-04-03 2013-06-19 北京科技大学 一种制备30GPa%级复相钢的Q&PB热处理工艺
CN103276164B (zh) * 2013-05-15 2014-12-31 哈尔滨工业大学 一种中碳硅锰铬镍系低合金钢高强韧化热处理方法
MX2015015332A (es) * 2013-05-17 2016-07-15 Ak Steel Properties Inc Acero de alta resistencia que exhibe buena ductilidad y metodo de produccion via temple y tratamiento de particion mediante baño de zinc.
WO2015011511A1 (fr) * 2013-07-24 2015-01-29 Arcelormittal Investigación Y Desarrollo Sl Tôle d'acier à très hautes caractéristiques mécaniques de résistance et de ductilité, procédé de fabrication et utilisation de telles tôles
WO2016001704A1 (fr) * 2014-07-03 2016-01-07 Arcelormittal Procédé de fabrication d'une tôle d'acier à haute résistance et tôle ainsi obtenue
WO2016001710A1 (fr) * 2014-07-03 2016-01-07 Arcelormittal Procédé de fabrication d'un acier revêtu à haute résistance ayant une résistance et une ductilité améliorée et tôle obtenue
WO2016001702A1 (fr) 2014-07-03 2016-01-07 Arcelormittal Procédé de fabrication d'une tôle d'acier revêtue à haute résistance présentant une résistance, une ductilité et une formabilité améliorées
WO2016001700A1 (fr) * 2014-07-03 2016-01-07 Arcelormittal Procédé de production d'une tôle d'acier à haute résistance présentant une résistance, une ductilité et une aptitude au formage améliorées
WO2016001706A1 (fr) 2014-07-03 2016-01-07 Arcelormittal Procédé de fabrication d'une tôle d'acier haute résistance ayant une résistance et une aptitude au formage améliorées et feuille ainsi obtenue
WO2016020714A1 (fr) * 2014-08-07 2016-02-11 Arcelormittal Procédé permettant de produire une tôle d'acier revêtue présentant une meilleure résistance, une meilleure ductilité et une meilleure aptitude au formage
ES2674133T3 (es) * 2014-12-01 2018-06-27 Voestalpine Stahl Gmbh Procedimiento para el tratamiento térmico de un producto de manganeso-acero
CN104532126B (zh) * 2014-12-19 2017-06-06 宝山钢铁股份有限公司 一种低屈强比超高强度热轧q&p钢及其制造方法
WO2017109541A1 (fr) * 2015-12-21 2017-06-29 Arcelormittal Procédé de production d'une tôle d'acier revêtue de haute résistance présentant une ductilité et une aptitude au formage améliorées, et tôle d'acier revêtue ainsi obtenue
MA43505B1 (fr) * 2015-12-29 2020-06-30 Arcelormittal Procédé destiné à la production d'une tôle d'acier recuite après galvanisation à très haute résistance et tôle d'acier recuite après galvanisation obtenue
JP6967628B2 (ja) * 2015-12-29 2021-11-17 アルセロールミタル 超高強度合金化溶融亜鉛めっき鋼板を製造するための方法、及び得られた合金化溶融亜鉛めっき鋼板
US10619223B2 (en) 2016-04-28 2020-04-14 GM Global Technology Operations LLC Zinc-coated hot formed steel component with tailored property
EP3467135B1 (fr) * 2016-08-10 2020-09-23 JFE Steel Corporation Tôle d'acier mince, et procédé de fabrication de celle-ci
EP3476962B1 (fr) * 2016-08-10 2020-09-16 JFE Steel Corporation Tôle d'acier mince, et procédé de fabrication de celle-ci
WO2018055425A1 (fr) * 2016-09-22 2018-03-29 Arcelormittal Tôle d'acier de résistance et formabilité élevées et procédé de fabrication
CN107480328B (zh) * 2017-07-04 2022-09-20 山东建筑大学 一种基于q＆p工艺的碳配分理论计算方法
CN110997961B (zh) * 2017-08-22 2022-02-25 蒂森克虏伯钢铁欧洲股份公司 Q＆p钢用于生产磨损应用的成型组件的用途
DE102017216572A1 (de) 2017-09-19 2019-03-21 Thyssenkrupp Ag Schmelztauchbeschichtetes Stahlband mit verbessertem Oberflächenerscheinungsbild und Verfahren zu seiner Herstellung
EP3704276B1 (fr) * 2017-11-02 2022-09-21 Cleveland-Cliffs Steel Properties Inc. Acier estampé à chaud ayant des propriétés particulières après un traitement thermique innovant
EP3704281A1 (fr) 2017-11-02 2020-09-09 AK Steel Properties, Inc. Acier trempé sous presse ayant des propriétés sur mesure
CN111542635B (zh) * 2017-12-28 2022-07-01 通用汽车环球科技运作有限责任公司 具有增强的抗氧化性的用于热冲压的钢
WO2019180492A1 (fr) * 2018-03-23 2019-09-26 Arcelormittal Pièce forgée en acier bainitique et son procédé de fabrication
EP3786310A4 (fr) * 2018-04-23 2022-01-19 Nippon Steel Corporation Élément en acier et son procédé de production
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
US11612926B2 (en) 2018-06-19 2023-03-28 GM Global Technology Operations LLC Low density press-hardening steel having enhanced mechanical properties
CN110878401B (zh) * 2018-09-05 2021-06-22 山东建筑大学 一种1300MPa级稀土逆转变Q＆P钢制备方法
CN109338241B (zh) * 2018-10-18 2019-12-06 钢铁研究总院 一种2000MPa级M3型高韧塑性无镍钢及其制备方法
CN109365785A (zh) * 2018-11-29 2019-02-22 山东建筑大学 一种双向锤式破碎机锤头及其制造方法
EP3754037B1 (fr) * 2019-06-17 2022-03-02 Tata Steel IJmuiden B.V. Procédé de traitement thermique d'une bande d'acier laminée à froid à haute résistance
US11530469B2 (en) 2019-07-02 2022-12-20 GM Global Technology Operations LLC Press hardened steel with surface layered homogenous oxide after hot forming
CA3149331A1 (fr) * 2019-08-07 2021-02-11 United States Steel Corporation Produits en tole d'acier zinguee a ductilite elevee
CN111593258A (zh) * 2019-12-16 2020-08-28 北京特冶工贸有限责任公司 一种曲线用高耐磨高强韧贝马复相组织钢轨及其制造方法
CN116287965B (zh) * 2021-12-20 2024-07-23 四川大学 一种V-Ti-N微合金化高强钢及其P-Q&P工艺
CN115478225A (zh) * 2022-10-13 2022-12-16 武汉科技大学 一种1180MPa级短时间热轧淬火配分钢及其制备方法和应用

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2258886A1 (fr) 2008-01-31 2010-12-08 JFE Steel Corporation Tôle d'acier galvanisée par immersion à chaud, à haute résistance, présentant une excellente aptitude au traitement et son procédé de fabrication
EP2267176A1 (fr) 2008-02-08 2010-12-29 JFE Steel Corporation Tôle d'acier galvanisée à chaud à résistance élevée présentant une excellente aptitude au traitement et son procédé de fabrication
EP2325346A1 (fr) 2008-09-10 2011-05-25 JFE Steel Corporation Plaque d'acier à haute résistance et son procédé de fabrication

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4608822B2 (ja) * 2001-07-03 2011-01-12 Ｊｆｅスチール株式会社 プレス成形性と歪時効硬化特性に優れた高延性溶融亜鉛めっき鋼板およびその製造方法
ES2568649T3 (es) * 2004-01-14 2016-05-03 Nippon Steel & Sumitomo Metal Corporation Chapa de acero de alta resistencia galvanizada en caliente con excelente adherencia del baño y capacidad de expansión de agujeros y método de producción de la misma
JP4510488B2 (ja) * 2004-03-11 2010-07-21 新日本製鐵株式会社 成形性および穴拡げ性に優れた溶融亜鉛めっき複合高強度鋼板およびその製造方法
CA2697226C (fr) * 2007-10-25 2015-12-15 Jfe Steel Corporation Tole d'acier zinguee par immersion a chaud de haute resistance presentant une excellente aptitude au faconnage et son procede de fabrication

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2258886A1 (fr) 2008-01-31 2010-12-08 JFE Steel Corporation Tôle d'acier galvanisée par immersion à chaud, à haute résistance, présentant une excellente aptitude au traitement et son procédé de fabrication
EP2267176A1 (fr) 2008-02-08 2010-12-29 JFE Steel Corporation Tôle d'acier galvanisée à chaud à résistance élevée présentant une excellente aptitude au traitement et son procédé de fabrication
EP2325346A1 (fr) 2008-09-10 2011-05-25 JFE Steel Corporation Plaque d'acier à haute résistance et son procédé de fabrication

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
J.G. SPEER ET AL.: "Progress in the Global Development of the Quenching and Partitioning Process", PROCEEDINGS OF THE 17TH INTERNATIONAL FEDERATION FOR HEAT TREATMENT AND SURFACE ENGINEERING CONGRESS, vol. 2, 27 October 2008 (2008-10-27), Kobe, Japan, pages 415 - 422, XP055258795

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3175005B1 (fr) * 2014-07-30 2024-03-20 ArcelorMittal Procédé de fabrication d'une pièce en acier à haute résistance
US11136656B2 (en) 2015-05-21 2021-10-05 Cleveland-Cliffs Steel Properties Inc. High manganese 3rd generation advanced high strength steels
CN106244924A (zh) * 2016-08-31 2016-12-21 东北大学 一种冷轧淬火延性钢及制备方法
CN106244924B (zh) * 2016-08-31 2017-12-29 东北大学 一种冷轧淬火延性钢及制备方法
EP3899067B1 (fr) * 2018-12-18 2023-09-13 ArcelorMittal Tôle d'acier laminée à froid traitée thermiquement et son procédé de fabrication
WO2023170245A1 (fr) * 2022-03-10 2023-09-14 Tata Steel Nederland Technology B.V. Tôle d'acier à haute résistance présentant une excellente extensibilité de trou et son procédé de production

Also Published As

Publication number Publication date
WO2012120020A1 (fr) 2012-09-13
EP2683839A1 (fr) 2014-01-15
ES2535420T3 (es) 2015-05-11

Similar Documents

Publication Publication Date Title
EP2683839B1 (fr) Procédé pour produire un acier formable à haute résistance et acier formable à haute résistance produit par celui-ci
CN110088342B (zh) 具有高成形性的高强度冷轧钢板及其制造方法
CA2805834C (fr) Tole d&#39;acier laminee a froid, a haute resistance, dotee d&#39;une ouvrabilite et d&#39;une resistance aux chocs remarquables, et son procede de fabrication
CN101649415B (zh) 加工性优异的高强度钢板
US9732404B2 (en) Method of producing high-strength steel plates with excellent ductility and plates thus produced
WO2019092578A1 (fr) Tôle d&#39;acier laminée à froid et son procédé de fabrication
CN104513927B (zh) 一种抗拉强度800MPa级高强度高韧性钢板及其制造方法
EP3221476A1 (fr) Procédé de fabrication d&#39;un produit en acier haute résistance et produit en acier ainsi obtenu
EP3707283A1 (fr) Tôle d&#39;acier laminée à froid traitée thermiquement et son procédé de fabrication
WO2013144373A1 (fr) Tôle d&#39;acier laminée à froid à haute résistance acier et son procédé de production
CN101960038A (zh) 冷轧钢板
CN111148853B (zh) 扁钢产品及其制造方法
WO2021089851A1 (fr) Produit en acier au manganèse à haute résistance et son procédé de fabrication
Krizan et al. Development of third generation advanced high strength steels for automotive applications
CN111771009A (zh) 一种汽车钢及其制造方法
Sugimoto et al. TRIP aided and complex phase steels
CN113316650B (zh) 高强度钢带材
CN110621794B (zh) 具有优异延展性和可拉伸翻边性的高强度钢片
US20220205058A1 (en) A high strength steel product and a process to produce a high strength steel product
JP5365758B2 (ja) 鋼板及びその製造方法
UA125769C2 (uk) Холоднокатана листова сталь з нанесеним покриттям і спосіб її виготовлення
JPH1060593A (ja) 強度−伸びフランジ性バランスにすぐれる高強度冷延鋼板及びその製造方法
CN113840930A (zh) 经冷轧和涂覆的钢板及其制造方法
CA3138625C (fr) Tole d&#39;acier laminee a froid et revetue et son procede de fabrication
KR20200129163A (ko) 저합금 3세대 첨단 고강도 강 및 제조방법

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20131007

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

DAX Request for extension of the european patent (deleted)
RIC1 Information provided on ipc code assigned before grant

Ipc: C21D 9/46 20060101ALI20140730BHEP

Ipc: C21D 8/02 20060101AFI20140730BHEP

Ipc: C23C 2/06 20060101ALI20140730BHEP

Ipc: C23C 2/28 20060101ALI20140730BHEP

Ipc: C23C 2/02 20060101ALI20140730BHEP

Ipc: C22C 38/04 20060101ALI20140730BHEP

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20141006

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: TATA STEEL NEDERLAND TECHNOLOGY B.V.

INTG Intention to grant announced

Effective date: 20150202

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2535420

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20150511

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602012006331

Country of ref document: DE

Effective date: 20150513

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 719129

Country of ref document: AT

Kind code of ref document: T

Effective date: 20150515

REG Reference to a national code

Ref country code: NL

Ref legal event code: VDEP

Effective date: 20150401

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150803

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150701

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150702

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150801

REG Reference to a national code

Ref country code: DE

Ref legal event code: R026

Ref document number: 602012006331

Country of ref document: DE

PLBI Opposition filed

Free format text: ORIGINAL CODE: 0009260

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

26 Opposition filed

Opponent name: ARCELORMITTAL

Effective date: 20151223

Opponent name: THYSSENKRUPP STEEL EUROPE AG

Effective date: 20151229

PLAX Notice of opposition and request to file observation + time limit sent

Free format text: ORIGINAL CODE: EPIDOSNOBS2

REG Reference to a national code

Ref country code: AT

Ref legal event code: UEP

Ref document number: 719129

Country of ref document: AT

Kind code of ref document: T

Effective date: 20150401

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

Ref country code: RO

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20150401

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 5

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

PLAF Information modified related to communication of a notice of opposition and request to file observations + time limit

Free format text: ORIGINAL CODE: EPIDOSCOBS2

PLAB Opposition data, opponent's data or that of the opponent's representative modified

Free format text: ORIGINAL CODE: 0009299OPPO

R26 Opposition filed (corrected)

Opponent name: ARCELORMITTAL

Effective date: 20151223

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160307

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PLAB Opposition data, opponent's data or that of the opponent's representative modified

Free format text: ORIGINAL CODE: 0009299OPPO

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

R26 Opposition filed (corrected)

Opponent name: ARCELORMITTAL

Effective date: 20151223

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160331

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160331

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160307

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 6

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: SE

Payment date: 20170329

Year of fee payment: 6

Ref country code: FR

Payment date: 20170327

Year of fee payment: 6

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: AT

Payment date: 20170221

Year of fee payment: 6

Ref country code: GB

Payment date: 20170327

Year of fee payment: 6

Ref country code: BE

Payment date: 20170327

Year of fee payment: 6

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20170329

Year of fee payment: 6

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: ES

Payment date: 20170328

Year of fee payment: 6

REG Reference to a national code

Ref country code: DE

Ref legal event code: R064

Ref document number: 602012006331

Country of ref document: DE

Ref country code: DE

Ref legal event code: R103

Ref document number: 602012006331

Country of ref document: DE

RDAF Communication despatched that patent is revoked

Free format text: ORIGINAL CODE: EPIDOSNREV1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

RDAG Patent revoked

Free format text: ORIGINAL CODE: 0009271

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: PATENT REVOKED

27W Patent revoked

Effective date: 20171107

GBPR Gb: patent revoked under art. 102 of the ep convention designating the uk as contracting state

Effective date: 20171107

REG Reference to a national code

Ref country code: BE

Ref legal event code: FP

Effective date: 20150423

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160331

REG Reference to a national code

Ref country code: AT

Ref legal event code: MA03

Ref document number: 719129

Country of ref document: AT

Kind code of ref document: T

Effective date: 20171107

REG Reference to a national code

Ref country code: SE

Ref legal event code: ECNC

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150401