EP1592816B1 - Procede de fabrication d une bande d acier dual-phase a structure ferrito-martensitique, laminee a froid et bande obtenue - Google Patents

Procede de fabrication d une bande d acier dual-phase a structure ferrito-martensitique, laminee a froid et bande obtenue Download PDF

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Publication number
EP1592816B1
EP1592816B1 EP04706710.3A EP04706710A EP1592816B1 EP 1592816 B1 EP1592816 B1 EP 1592816B1 EP 04706710 A EP04706710 A EP 04706710A EP 1592816 B1 EP1592816 B1 EP 1592816B1
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EP
European Patent Office
Prior art keywords
strip
temperature
cooling
cold
rolled
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.)
Expired - Lifetime
Application number
EP04706710.3A
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German (de)
English (en)
French (fr)
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EP1592816A1 (fr
Inventor
Antoine Moulin
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.)
ArcelorMittal France SA
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ArcelorMittal France SA
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Publication date
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Publication of EP1592816A1 publication Critical patent/EP1592816A1/fr
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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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • 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
    • 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
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a process for manufacturing a dual-phase steel strip with a ferrito-martensitic structure, cold rolled, and the strip obtainable by this process, which is more particularly intended for the manufacture of parts for automobiles. by deep drawing.
  • Very high strength steels have been developed in recent years, in particular to meet the specific needs of the automotive industry, which are in particular to reduce the weight and therefore the thickness of parts, and improve safety. which involves increasing the fatigue strength and impact resistance of the parts. These improvements should not further deteriorate the formability of the sheets used for the manufacture of the parts.
  • EP0969112 is a patent which provides high strength steel sheets with high impact energy absorption properties, as steel materials, for use in shaping and working in parts such as automobile front end elements which absorb impact energy in a collision, as well as a method for their production.
  • the high strength steel sheets of the invention which exhibit high impact energy absorption properties are high strength steel sheets with high flow stress during dynamic deformation, characterized by that the microstructure of the steel sheets in their final form is a composite microstructure of a mixture of ferrite and / or bainite, one of the phases of which is dominant, and a third phase comprising austenite retained in a fraction volume between 3% and 50%, in which the mean value ⁇ dyn (MPa) of the flow stress in the range of 3 - 10% of the equivalent stress when deformed in a strain rate range of 5 ⁇ 102 - 5 ⁇ 103 (1 / s) after predeformation greater than 0% and less than or equal to 10% of the equivalent stress, satisfies the inequality: ⁇ dyn ⁇ 0766 ⁇ TS + 250 expressed in terms of maximum stress TS (MPa) in the static tensile test measured in a strain rate range of 5 ⁇ 10-4 - 5 ⁇ 10-3 (1 / s) without strain, and the working quench coefficient
  • the object of the present invention is to remedy the drawbacks of steels of the prior art by providing a steel strip suitable for deep drawing, and having both excellent mechanical characteristics and excellent anisotropy characteristics. .
  • a third object of the invention is the use of a steel strip according to the invention, for the manufacture of automobile parts by deep drawing.
  • the process according to the invention consists in hot rolling a slab of specific composition, then in winding the hot strip obtained at a temperature between 550 and 850 ° C.
  • This high temperature winding is in fact favorable to the development of what is called a texture, that is to say an anisotropic structure.
  • a texture that is to say an anisotropic structure.
  • Such a coil in fact makes it possible to coalesce the precipitation of cementite Fe3C, and to reduce the quantity of carbon put back into solution during annealing, which is harmful to the development of the recrystallization texture.
  • the process then consists in cold rolling the strip with a reduction rate of between 60 and 90%, then in annealing the strip continuously in the intercritical domain.
  • Intercritical annealing makes it possible to re-dissolve the majority of the carburized phases formed during the winding after recrystallization.
  • the fact that the austenitization and the dissolution of the carburized phases take place after the recrystallization makes it possible to keep the carbon trapped during the recrystallization and to release it once the texture of the recrystallized ferrite is developed.
  • the texture will therefore not be affected by the carbon in solid solution, as in the case of a low temperature coil, but only affected by the isotropic nature of the martensite formed.
  • the method then consists in cooling the strip to ambient temperature, in one or more steps, the cooling rate between 600 ° C and ambient temperature being between 100 ° C / s and 1500 ° C / s, and optionally in subjecting it to tempering at a temperature below 300 ° C.
  • Quenching with water makes it possible to form large proportions of carburized phases with respect to the analysis considered.
  • the fraction of martensitic phase formed can be reduced by lowering the holding temperature to lower values in the intercritical range, or even by practicing slow cooling before quenching.
  • the difference in hardness between the ferritic matrix and the martensitic phase can also be reduced, by cooling the strip more slowly or by applying a short tempering, of the order of one minute, of the martensitic phase formed after quenching with water. .
  • this income is in no case an overaging treatment as found in the prior art.
  • these overaging treatments which are generally carried out between 300 and 500 ° C., have the particular effect of removing martensite which is an essential element of the present invention.
  • the tempering optionally practiced according to the invention consists in precipitating part of the carbon in solid solution trapped in the martensite, without reducing the proportion of this martensite.
  • the maximum temperature of this tempering is 300 ° C, preferably 250 ° C, and more particularly preferably 200 ° C.
  • composition according to the invention comprises carbon in a content of between 0.010% and 0.100%. This element is essential for obtaining good mechanical characteristics, but must not be present in too large a quantity, because it would generate the formation of too large a proportion of martensitic phase.
  • Manganese in a content of between 0.050% and 1.0%. Manganese improves the elastic limit of steel while greatly reducing its ductility, for which its content is limited.
  • the composition also includes chromium in a content of between 0.010% and 1.0% which aids in the desired formation of martensite.
  • the composition also comprises silicon in a content of between 0.010% and 0.50%. It greatly improves the elastic limit of steel while weakly reducing its ductility and deteriorating its coatability.
  • the composition also includes phosphorus in a content between 0.001% and 0.20%, which hardens the microstructure without affecting its texture.
  • the composition also comprises aluminum at a content of between 0.010% and 0.10% which prevents aging by trapping nitrogen.
  • the two shades were austenitized at 1250 ° C. for one hour, in order to obtain a dissolution of the aluminum nitrides.
  • the slabs were then hot-rolled so that the end-of-rolling temperature was greater than 900 ° C., the value of AR3 being approximately 870 ° C. for the two grades.
  • the hot-rolled strips were then cooled by quenching in water, at a cooling rate of the order of 25 ° C / s, until the winding temperature was reached.
  • Grade A was wound at 720 ° C, while one sample of grade B was wound at 550 ° C and the other at 720 ° C.
  • the various samples were then cold rolled until a reduction rate of 75% was reached, then were subjected to an annealing treatment at a holding temperature of 750 ° C for certain samples, and of 800 ° C for d 'other.
  • the cooling to ambient temperature is then carried out at a speed of the order of 25 ° C./s, by quenching with water.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Metal Rolling (AREA)
EP04706710.3A 2003-02-05 2004-01-30 Procede de fabrication d une bande d acier dual-phase a structure ferrito-martensitique, laminee a froid et bande obtenue Expired - Lifetime EP1592816B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
FR0301358A FR2850671B1 (fr) 2003-02-05 2003-02-05 Procede de fabrication d'une bande d'acier dual-phase a structure ferrito-martensitique, laminee a froid et bande obtenue
FR0301358 2003-02-05
PCT/FR2004/000209 WO2004079022A1 (fr) 2003-02-05 2004-01-30 Procede de fabrication d'une bande d'acier dual-phase a structure ferrito-martensitique, laminee a froid et bande obtenue

Publications (2)

Publication Number Publication Date
EP1592816A1 EP1592816A1 (fr) 2005-11-09
EP1592816B1 true EP1592816B1 (fr) 2020-10-14

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EP04706710.3A Expired - Lifetime EP1592816B1 (fr) 2003-02-05 2004-01-30 Procede de fabrication d une bande d acier dual-phase a structure ferrito-martensitique, laminee a froid et bande obtenue

Country Status (16)

Country Link
US (1) US20060144482A1 (enExample)
EP (1) EP1592816B1 (enExample)
JP (1) JP4528769B2 (enExample)
KR (1) KR101091021B1 (enExample)
CN (1) CN100465299C (enExample)
BR (1) BRPI0407236A (enExample)
CA (1) CA2514736C (enExample)
ES (1) ES2831249T3 (enExample)
FR (1) FR2850671B1 (enExample)
HU (1) HUE052206T2 (enExample)
MX (1) MXPA05008189A (enExample)
PL (1) PL206109B1 (enExample)
RU (1) RU2341566C2 (enExample)
UA (1) UA87454C2 (enExample)
WO (1) WO2004079022A1 (enExample)
ZA (1) ZA200505968B (enExample)

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DE102013013067A1 (de) * 2013-07-30 2015-02-05 Salzgitter Flachstahl Gmbh Siliziumhaltiger, mikrolegierter hochfester Mehrphasenstahl mit einer Mindestzugfestigkeit von 750 MPa und verbesserten Eigenschaften und Verfahren zur Herstellung eines Bandes aus diesem Stahl
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CN103952523B (zh) * 2014-04-15 2016-01-20 东北大学 一种马氏体铁素体双相钢冷轧板带的连续退火方法
PL3164516T3 (pl) 2014-07-03 2019-10-31 Arcelormittal Sposób wytwarzania powlekanej albo niepowlekanej blachy stalowej o ultra wysokiej wytrzymałości i uzyskana blacha
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Also Published As

Publication number Publication date
FR2850671A1 (fr) 2004-08-06
PL206109B1 (pl) 2010-07-30
ES2831249T3 (es) 2021-06-08
EP1592816A1 (fr) 2005-11-09
CN1748039A (zh) 2006-03-15
KR101091021B1 (ko) 2011-12-09
KR20050095782A (ko) 2005-09-30
US20060144482A1 (en) 2006-07-06
CA2514736C (fr) 2012-12-04
PL377834A1 (pl) 2006-02-20
JP4528769B2 (ja) 2010-08-18
CN100465299C (zh) 2009-03-04
HUE052206T2 (hu) 2021-04-28
RU2341566C2 (ru) 2008-12-20
MXPA05008189A (es) 2005-10-05
RU2005127577A (ru) 2006-02-10
WO2004079022A1 (fr) 2004-09-16
CA2514736A1 (fr) 2004-09-16
ZA200505968B (en) 2006-06-28
UA87454C2 (ru) 2009-07-27
JP2006520431A (ja) 2006-09-07
FR2850671B1 (fr) 2006-05-19
BRPI0407236A (pt) 2006-01-31

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