EP2683839B1 - Verfahren zur herstellung von hochfestem formbarem stahl und damit hergestellter hochfester formbarer stahl - Google Patents

Verfahren zur herstellung von hochfestem formbarem stahl und damit hergestellter hochfester formbarer stahl Download PDF

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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
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Prior art keywords
strip
martensite
temperature
austenite
carbon
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EP2683839A1 (de
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David Neal Hanlon
Stefanus Matheus Cornelis VAN BOHEMEN
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Tata Steel Nederland Technology BV
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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
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—Modifying the physical properties of ferrous metals or ferrous alloys 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.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical 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. Verfahren zum Herstellen von abgeschrecktem und partitioniertem Stahl durch Bereitstellen eines kaltgewalzten und geglühten Stahlbandes, der (in Gew.-%) folgendes enthält:
    • 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
    • wobei der Rest Eisen und unvermeidbare Verunreinigungen ist,
    wobei der Glühprozess die folgenden Schritte umfasst:
    (i) Wiedererhitzen des kaltgewalzten Bandes auf eine Glühtemperatur T1 zwischen Ac3 - 40 und Ac3 +80;
    (ii) Halten des Bandes auf T1 über eine Glühzeit t1 zwischen 10 und 200 Sekunden;
    (iii) Kühlen des geglühten Streifens mit der kritischen Kühlrate CR1, um eine Bildung von Ferrit und Perlit zu vermeiden, auf eine Abschreckungstemperatur T2, um eine Mikrostruktur in dem Band zu erzeugen, die einen Martensitanteil und einen Restaustenitanteil umfasst;
    (iv) repartitionierendes Glühen des gekühlten Bandes auf einer Temperatur T3, um das Austenit in Kohlenstoff anzureichern durch Repartitionierung des Kohlenstoffs aus dem Martensit auf den Austenitanteil über eine Repartitionierungszeit t2 zwischen 20 und 500 Sekunden, wobei der Martensitanteil zu Beginn des repartitionierenden Glühens zwischen 60 und 90 % der Mikrostruktur liegt, wobei (Ms-70) < T3 ≤ (Ms+50);
    (v) Kühlen des Bandes mit einer Kühlrate CR2 auf Umgebungstemperatur.
  2. Verfahren nach Anspruch 1, wobei CR1 mindestens 30 °C/s beträgt.
  3. Verfahren nach Anspruch 1 oder 2, wobei der Martensitanteil zu Beginn des repartitionierenden Glühens höchstens 85% der Mikrostruktur beträgt.
  4. Verfahren nach einem der vorstehenden Ansprüche, wobei: AC 3 - 40 < T 1 ≤ AC 3 + 50 für Kohlenstoff zwischen 0 , 18 - 0 , 3 % C ;
    Figure imgb0010
    oder AC 3 - 20 < T 1 ≤ AC 3 + 30 für Kohlenstoff zwischen 0 , 3 bis 0 , 4 % C .
    Figure imgb0011
  5. Verfahren nach einem der vorstehenden Ansprüche, wobei T1 größer ist als Ac3.
  6. Verfahren nach einem der vorstehenden Ansprüche, wobei der kaltgewalzte Band höchstens 0,5 % Al enthält.
  7. Verfahren nach einem der vorstehenden Ansprüche, wobei der kaltgewalzte Band mindestens 0,25 % C und mindestens 0,01 % Al enthält.
  8. Verfahren nach einem der vorstehenden Ansprüche, wobei T2 gleich T3 ist.
  9. Verfahren nach einem der Ansprüche 1 bis 7, wobei T2 kleiner ist als T3.
  10. Verfahren nach einem der vorstehenden Ansprüche, wobei der kaltgewalzte und geglühte Band mit einer oder mehreren metallischen Schicht(en) überzogen ist, wobei der Schritt des Bereitstellens des metallischen Überzugs vorzugsweise durch Feuerverzinkung oder galvanische Verzinkung erfolgt.
  11. Stahlband, der durch ein Verfahren nach einem der Ansprüche 1 bis 10 erzeugt worden ist, wobei der Stahl eine Mikrostruktur aufweist, die mindestens 5 % Austenit enthält, wobei die Mikrostruktur 60 bis 90 % (Volumenprozent) wärmebehandeltes Martensit enthält, und wobei ein e-Verhältnis von mindestens 1,8 und eine Zugfestigkeit (UTS) von mindestens 900 MPa gegeben sind, wobei das e-Verhältnis definiert ist als egemessen/eberechnet, und wobei eberechnet wie folgt berechnet wird: e berechnet = k ⁢ 1 UTS 2
    Figure imgb0012
     und wobei egemessen der an einem Probenstück mit einer Dicke von 1 mm gemessenen Elongation bei einer Messlänge von 80 mm entspricht, oder wobei egemessen der an einer anderen Geometrie gemessenen Elongation entspricht, und umgewandelt in eine äquivalente Elongation bei einer Messlänge von 80 mm und einer Dicke von 1 mm unter Verwendung von: e 2 = e 1 L 1 L 2 ⋅ A 2 A 1 m
    Figure imgb0013
  12. Stahlband nach Anspruch 11, wobei die Mikrostruktur ferne eines oder mehrere der aus Bainit, Martensit, angelassenem Martensit, Ferrit, feinen Carbiden enthält.
  13. Stahlband nach Anspruch 11 oder 12, wobei die Mikrostruktur kein Ferrit und/oder grobes Cementit enthält.
  14. Stahlband nach einem der Ansprüche 11 bis 13, wobei das Verhältnis der Streckgrenze zur Zugfestigkeit mindestens 0,6 beträgt.
EP12708008.3A 2011-03-07 2012-03-07 Verfahren zur herstellung von hochfestem formbarem stahl und damit hergestellter hochfester formbarer stahl Revoked EP2683839B1 (de)

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EP11157239 2011-03-07
PCT/EP2012/053856 WO2012120020A1 (en) 2011-03-07 2012-03-07 Process for producing high strength formable steel and high strength formable steel produced therewith
EP12708008.3A EP2683839B1 (de) 2011-03-07 2012-03-07 Verfahren zur herstellung von hochfestem formbarem stahl und damit hergestellter hochfester formbarer stahl

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Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2258886A1 (de) 2008-01-31 2010-12-08 JFE Steel Corporation Hochfestes heissverzinktes stahlblech mit hervorragender verarbeitbarkeit und herstellungsverfahren dafür
EP2267176A1 (de) 2008-02-08 2010-12-29 JFE Steel Corporation Hochfestes heissverzinktes stahlblech mit hervorragender verarbeitbarkeit und herstellungsverfahren dafür
EP2325346A1 (de) 2008-09-10 2011-05-25 JFE Steel Corporation Hochfeste stahlplatte und herstellungsverfahren dafür

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
WO2005068676A1 (ja) * 2004-01-14 2005-07-28 Nippon Steel Corporation めっき密着性および穴拡げ性に優れた溶融亜鉛めっき高強度鋼板とその製造方法
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
EP2202327B1 (de) * 2007-10-25 2020-12-02 JFE Steel Corporation Herstellungsverfahren für hochfestes galvanisiertes stahlblech mit hervorragender formbarkeit

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2258886A1 (de) 2008-01-31 2010-12-08 JFE Steel Corporation Hochfestes heissverzinktes stahlblech mit hervorragender verarbeitbarkeit und herstellungsverfahren dafür
EP2267176A1 (de) 2008-02-08 2010-12-29 JFE Steel Corporation Hochfestes heissverzinktes stahlblech mit hervorragender verarbeitbarkeit und herstellungsverfahren dafür
EP2325346A1 (de) 2008-09-10 2011-05-25 JFE Steel Corporation Hochfeste stahlplatte und herstellungsverfahren dafür

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 (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3663415A1 (de) * 2014-07-03 2020-06-10 ArcelorMittal Verfahren zur herstellung eines hochfesten stahlblechs mit verbesserter festigkeit, dehnbarkeit und verformbarkeit
EP3175005B1 (de) * 2014-07-30 2024-03-20 ArcelorMittal Ein verfahren zur herstellung eines hochfesten stahlstücks
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 (de) * 2018-12-18 2023-09-13 ArcelorMittal Kaltgewalztes und wärmebehandeltes stahlblech und verfahren zur herstellung davon
WO2023170245A1 (en) * 2022-03-10 2023-09-14 Tata Steel Nederland Technology B.V. High strength steel sheet with excellent hole expandability and method of producing the same

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