EP2649214B1 - Procédé de fabrication d'un acier à haute teneur en manganèse présentant une résistance mécanique et une aptitude au formage élevées, et acier obtenu par le procédé - Google Patents

Procédé de fabrication d'un acier à haute teneur en manganèse présentant une résistance mécanique et une aptitude au formage élevées, et acier obtenu par le procédé Download PDF

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EP2649214B1
EP2649214B1 EP11820814.9A EP11820814A EP2649214B1 EP 2649214 B1 EP2649214 B1 EP 2649214B1 EP 11820814 A EP11820814 A EP 11820814A EP 2649214 B1 EP2649214 B1 EP 2649214B1
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Prior art keywords
steel
annealing
optionally
twip
content
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EP11820814.9A
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German (de)
English (en)
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EP2649214A2 (fr
Inventor
Alessandro Ferraiuolo
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Centro Sviluppo Materiali SpA
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Centro Sviluppo Materiali SpA
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    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/561—Continuous furnaces for strip or wire with a controlled atmosphere or vacuum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • 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

Definitions

  • the present invention refers to the field of products made of high manganese content austenitic steel and with high mechanical resistance and high formability (steels named as TWIP, Twinning Induced Plasticity).
  • TWIP type steels constitute within high resistance steel field a unique family being characterized in that the same display peculiar mechanical properties.
  • TWIP steels have austenitic structure with face-centered cubic lattice (FCC) along with a low stacking fault energy (SFE) promoting the activation of twinning deformation mechanisms (mechanically induced twinning).
  • FCC face-centered cubic lattice
  • SFE stacking fault energy
  • the atoms of solute interact with dislocations through two mechanisms:
  • this TWIP steel type in particular in strip form, is particularly appreciated in the automotive field.
  • the TWIP steel strips allow the manufacturing of complexly shaped automotive components in a relatively simple way and use thereof under conditions requiring high mechanical performances, in particular for parts involved in energy absorption and structure reinforcing.
  • compositions for single alloy elements or combinations of alloy elements, independently from each other are:
  • the proposed process comprises also the further operating step to produce a metallic coating on the hot obtained strip using a zinc based alloy containing magnesium and aluminium.
  • the steel according to the invention can be used for the manufacturing of complexly shaped components to be employed for energy absorption, structure reinforcing and in general terms for automotive applications.
  • Austenitic TWIP steel according to the invention optionally coated with zinc alloy, can be used in form of strip, sheet, bar, billet, pipe.
  • manganese plays a determining role in the stabilization of the austenitic phase. Compositionally the range thereof is 16-18% according to the present invention. In correspondence of this interval of Mn percentages the maximum stabilization of austenite is observed.
  • the silicon exerts the function to increase the mechanical resistance and ductility of the steel.
  • Si content is comprised between 0.05 and 2.0%. When the percentage thereof is lower than 0.05, often a thick iron and manganese oxide layer is formed resulting in increased pickling duration, and in decreased corrosion resistance of the annealed steel and surface quality of the cold rolled sheet. When the percentage thereof is higher than 2.0%, stability properties of the steel are decreased.
  • the aluminium presence is finalized to the increment of the ductility of the steel.
  • the content thereof in the austenitic steel according to the invention is comprised between 0.01 and 2.0%.
  • the content of Al is lower than 0.01%, the mechanical resistance is increased but a quick degradation of the ductility occurs.
  • it is present in percentage higher than 2.0%, the steel exhibits decreased ductility along with lower castability during the continuous casting and corrosion susceptibility during hot rolling with consequent worsening of the surface quality of the resulting product.
  • Nitrogen promotes the gemination generation, by means of reaction with aluminium and precipitation of fine nitrides (during the solidification) within the austenitic grains, the presence thereof improves both mechanical resistance and suitability to be elongated during the steel working. Nitrogen is present in the steel used according to the invention in percentage lower than 0.1%. In fact when the content of N is higher than 0.1%, excess nitride precipitation takes place resulting in cold machinability and formability degradation.
  • Nb+Co and Re+W promote the formation of geminations, and improve both the mechanical resistance and the suitability to be elongated during steel working.
  • the present invention in based on, it has been found that it is fundamental to control the activity of carbon in the atmosphere of annealing furnace in order a control of non-decarburizing or re-carburizing to be carried out.
  • a steel containing C 0.6; Mn 18; Ni 0.5; 0.3; Al 1.0; P+Sn+Sb+As 0.1; S+Se+Te 0.01; N 0.05; Nb+Co 0.1, apart from iron and unavoidable impurities, is subjected to the process according to the present invention.
  • a 1.0 mm thick strip of claimed steel is obtained using a continuous casting plant and it is hot rolled, cold rolled and subjected to recrystallization annealing according to the invention as reported hereinafter.
  • Continuous recrystallization annealing occurs at 1000°C for 90s in non-decarburizing atmosphere, carbon activity within annealing atmosphere is 0.15, nitrogen content is 100% and dew point -25°C.
  • the final product exhibits the following mechanical features: Rp0.2 290 MPa, Rm 1000 MPa and A80 90%, and has austenitic microstructure.
  • This product is used for the manufacturing of auto-motive components requiring high mechanical resistance and high formability, as for example car structural elements.
  • a steel containing C 0.6; Mn 17; Si 0.3; Al 0.04; P+Sn+Sb+As ⁇ 0.1; S+Se+Te 0.01; N 0.05; Re+W 0.2, apart from iron and unavoidable impurities, is subjected to the process according to the present invention.
  • a 2.0 mm thick tube made of this steel obtained using a continuous casting plant is hot rolled, cold rolled and subjected to recrystallization annealing according to the invention as reported hereinafter.
  • the recrystallization annealing is carried out in batch at 750°C for 180 minutes.
  • the carbon activity within annealing atmosphere is 0.15
  • the nitrogen percentage within the furnace is 95%
  • the dew point is - 30°C
  • hydrogen is 5%.
  • the final strip exhibits the following mechanical features Rp0.2 310 MPa, Rm 950 MPa and A80 80% and has austenitic microstructure.
  • This product is used for the preparation of automotive components requiring high mechanical resistance and high ductility, as for example structure reinforcing bars of cars.

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

Claims (6)

  1. Procédé de fabrication d'un acier austénitique à teneur élevée en Mn du type TWIP (plasticité induite par maclage), avec une résistance mécanique et une formabilité élevées, caractérisé en ce que l'acier a la composition chimique suivante, en pourcentage en poids : C 0,2-1,5 ; Mn 10-25 ; facultativement Ni < 2 ; Si 0,05-2,00 ; Al 0,01-2,0 ; 0,01 ≤ N < 0,1 ; P + Sn + Sb + As < 0,2 ;
    S + Se + Te < 0,5 ; et Nb + Co 0,1-0,4 et Re + W < 1, le reste étant du Fe à part les impuretés inévitables, et en ce que, après avoir été soumis à un laminage à froid, il est soumis à un recuit de recristallisation réalisé
    - pour un recuit continu, à une température dans l'intervalle de 900 °C-1100 °C pendant une durée de 60 secondes à 120 secondes, ou
    - pour un recuit en paquet, à une température dans l'intervalle de 700 °C-800 °C pendant une durée de 30 minutes à 400 minutes, l'atmosphère de recuit comprenant une activité carbone ac entre 0,1 et 1,0, une teneur en azote N2 entre 90 % et 100 % pour le recuit continu, ou entre 0 % et 100 % pour le recuit en paquet, une teneur en hydrogène H2 entre 0 et 10 % pour le recuit continu, ou entre 0 % et 100 % pour le recuit en paquet, le point de rosé pour le recuit continu et en paquet étant inférieur à 0 °C et de préférence entre -10 °C et -50 °C.
  2. Procédé selon la revendication 1, dans lequel les intervalles de composition préférés pour des éléments d'alliage simples ou pour une combinaison d'éléments d'alliage, indépendamment les uns des autres, sont :
    C 0,4-0,8 ; Mn 16-19 ; facultativement Ni < 1,0 ; Si 0,2-0,4 ; Al 0,1-1,5 ; N 0,01-0,05 ; et Nb + Co 0,1-0,4 et Re + W 0,3-0,7.
  3. Procédé selon la revendication 1 ou 2, comprenant l'opération supplémentaire de fabrication d'un revêtement métallique obtenu dans des conditions de chauffage par un alliage à base de zinc contenant du magnésium et de l'aluminium.
  4. Acier austénitique ayant une plasticité induite par maclage (TWIP), caractérisé en ce que l'acier a la composition chimique suivante, en pourcentage en poids :
    C 0,2-1,5 ; Mn 10-25 ; facultativement Ni < 2 ; Si 0, 05-2, 00 ; Al 0,01-2,0 ; 0,01 ≤ N < 0,1 ; P + Sn + Sb + As < 0,2 ; S + Se + Te < 0,5 ; et Nb + Co 0,1-0,4 et Re + W < 1, le reste étant du fer à part les impuretés inévitables avec les caractéristiques mécaniques suivantes :
    Rp 0,2 entre 250 et 350 MPa
    Rm entre 850 et 1100 MPa
    A80 entre 60 et 100 %.
  5. Acier austénitique selon la revendication 4, qui a la composition C 0,4-0,8 ; Mn 16-19 ; facultativement Ni < 1,0 ; Si 0,2-0,4 ; Al 0,1-1,5 ; N 0,01-0,05 ; et Nb + Co 0,1-0,4 et Re + W 0,3-0,7.
  6. Utilisation d'acier austénitique selon la revendication 4 ou 5 pour la fabrication de composants à géométrie complexe, pour l'absorption d'énergie, pour des renforcements structuraux et des applications automobiles.
EP11820814.9A 2010-12-07 2011-12-07 Procédé de fabrication d'un acier à haute teneur en manganèse présentant une résistance mécanique et une aptitude au formage élevées, et acier obtenu par le procédé Active EP2649214B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
ITRM2010A000641A IT1403129B1 (it) 2010-12-07 2010-12-07 Procedimento per la produzione di acciaio ad alto manganese con resistenza meccanica e formabilità elevate, ed acciaio così ottenibile.
PCT/IT2011/000401 WO2012077150A2 (fr) 2010-12-07 2011-12-07 Procédé de fabrication d'un acier à haute teneur en manganèse présentant une résistance mécanique et une aptitude au formage élevées, et acier obtenu par le procédé

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EP2649214A2 EP2649214A2 (fr) 2013-10-16
EP2649214B1 true EP2649214B1 (fr) 2016-12-07

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Country Status (5)

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EP (1) EP2649214B1 (fr)
KR (1) KR20140025324A (fr)
CN (1) CN103339279B (fr)
IT (1) IT1403129B1 (fr)
WO (1) WO2012077150A2 (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10774395B2 (en) 2015-05-22 2020-09-15 Outokumpu Oyj Method for manufacturing a component made of austenitic steel
US11247252B2 (en) 2015-07-16 2022-02-15 Outokumpu Oyj Method for manufacturing a component of austenitic TWIP or TRIP/TWIP steel

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DE102013003516A1 (de) 2013-03-04 2014-09-04 Outokumpu Nirosta Gmbh Verfahren zur Herstellung eines ultrahochfesten Werkstoffs mit hoher Dehnung
KR101657808B1 (ko) * 2014-12-22 2016-09-20 주식회사 포스코 단열성 전단띠 형성에 대한 저항성이 우수한 오스테나이트계 강재 및 이의 제조방법
TWI504756B (zh) 2015-01-30 2015-10-21 China Steel Corp Manufacture method of high strength and high ductility steel
EP3173504A1 (fr) 2015-11-09 2017-05-31 Outokumpu Oyj Procédé de fabrication d'un composant d'acier austenitique et utilisation dudit composant
EP3395979B1 (fr) 2015-12-24 2020-06-03 Posco Tôle d'acier à base d'austénite plaquée d'aluminium fondu ayant d'excellentes propriétés de plaquage et de soudabilité et son procédé de fabrication
CN105755388B (zh) * 2016-04-18 2018-04-24 和县隆盛精密机械有限公司 一种机械臂用高强度耐磨铸件的铸造方法
DE102016117494A1 (de) * 2016-09-16 2018-03-22 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines umgeformten Bauteils aus einem mittelmanganhaltigen Stahlflachprodukt und ein derartiges Bauteil
KR101903174B1 (ko) 2016-12-13 2018-10-01 주식회사 포스코 강도 및 연성이 우수한 저합금 강판
WO2018188766A1 (fr) 2017-04-11 2018-10-18 Thyssenkrupp Steel Europe Ag Produit plat en acier laminé à froid, recuit sur base, et procédé de fabrication s'y rapportant
CN107574377B (zh) * 2017-09-07 2019-05-03 北京科技大学 一种基于纳米结构的高吸能型高锰twip钢及其制备方法
KR101952818B1 (ko) 2017-09-25 2019-02-28 주식회사포스코 강도 및 연성이 우수한 저합금 강판 및 이의 제조방법
WO2019134102A1 (fr) * 2018-01-05 2019-07-11 The University Of Hong Kong Acier pour automobile et son procédé d'élaboration
CN117265419A (zh) * 2022-06-15 2023-12-22 宝山钢铁股份有限公司 强度1000-1600MPa的高成形性、易磷化高锰冷轧钢板及其制造方法

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10774395B2 (en) 2015-05-22 2020-09-15 Outokumpu Oyj Method for manufacturing a component made of austenitic steel
US11247252B2 (en) 2015-07-16 2022-02-15 Outokumpu Oyj Method for manufacturing a component of austenitic TWIP or TRIP/TWIP steel

Also Published As

Publication number Publication date
EP2649214A2 (fr) 2013-10-16
ITRM20100641A1 (it) 2012-06-08
WO2012077150A3 (fr) 2012-11-22
KR20140025324A (ko) 2014-03-04
CN103339279A (zh) 2013-10-02
CN103339279B (zh) 2016-09-28
WO2012077150A2 (fr) 2012-06-14
IT1403129B1 (it) 2013-10-04

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