US20060144482A1 - Method of producing a cold-rolled band of dual-phase steel with a ferritic/martensitic structure and band thus obtained - Google Patents

Method of producing a cold-rolled band of dual-phase steel with a ferritic/martensitic structure and band thus obtained Download PDF

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Publication number
US20060144482A1
US20060144482A1 US10/544,206 US54420604A US2006144482A1 US 20060144482 A1 US20060144482 A1 US 20060144482A1 US 54420604 A US54420604 A US 54420604A US 2006144482 A1 US2006144482 A1 US 2006144482A1
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Prior art keywords
strip
temperature
cooling
rolled
steel strip
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Abandoned
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US10/544,206
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English (en)
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Antoine Moulin
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USINOR SA
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Assigned to USINOR reassignment USINOR ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: MOULIN, ANTOINE
Publication of US20060144482A1 publication Critical patent/US20060144482A1/en
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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 producing a cold-rolled ferritic/martensitic dual-phase steel strip and to a strip that can be obtained by this process, which is more particularly intended for the production of automobile parts by deep drawing.
  • Ultrahigh-strength steels have been developed in recent years, especially so as to meet the specific requirements of the automobile industry, which are in particular the reduction in weight, and therefore in thickness, of the parts and the improvement in safety afforded by the increase in fatigue strength and impact behavior of the parts. These improvements must also not degrade the formability of the steel sheet used for producing the parts.
  • steels with a single-phase structure which have a high mean anisotropy coefficient r but have only moderate mechanical properties, with a tensile strength R m not exceeding 400 MPa.
  • the object of the present invention is to remedy the drawbacks of the steels of the prior art by proposing a steel strip capable of deep drawing and having at the same time excellent mechanical properties and excellent anisotropy characteristics.
  • the first subject of the invention is a process for producing a cold-rolled ferritic/martensitic dual-phase steel strip, characterized in that a slab, the chemical composition of which comprises, by weight:
  • the cooling rate between 600° C. and the ambient temperature being between 100° C./s and 1500° C./s;
  • the annealing and cooling operations being carried out in such a way that the strip finally contains from 1 to 15% martensite.
  • the chemical composition of the steel furthermore comprises, by weight:
  • the strip is hot rolled at a temperature above 850° C.
  • the strip is hot coiled at a temperature of between 550 and 750° C.
  • the strip is cold rolled with a reduction ratio of between 70 and 80%;
  • the continuous annealing of the cold-rolled strip comprises a temperature rise phase followed by a soak phase at a predetermined temperature
  • the soak temperature is between Ac 1 and 900° C.
  • the soak temperature is between 750 and 850° C.
  • the cooling down to the ambient temperature comprises a first, slow cooling step between the soak temperature and 600° C., during which the cooling rate is less than 50° C./s, followed by a second cooling step at a higher rate, of between 100° C./s and 1500° C./s, down to the ambient temperature.
  • the second subject of the invention is a cold-rolled ferritic/martensitic dual-phase steel strip, the chemical composition of which comprises, by weight:
  • composition of the strip is the following:
  • the steel according to the invention may also include the following features, by themselves or in combination:
  • the third subject of the invention is a steel strip according to the invention for the production of automobile parts by deep drawing.
  • the process according to the invention consists in hot rolling a slab of specific composition and then in coiling the hot-rolled strip obtained at a temperature of between 550 and 850° C.
  • This high-temperature coiling operation is favorable to the development of what is called a texture, that is to say an anisotropic structure. This is because such a coiling operation makes it possible for the Fe 3 C cementite precipitates to coalesce and to reduce the amount of carbon going back into solution during the anneal, this being detrimental to the development of the recrystallization texture.
  • Water quenching allows substantial proportions of carbide phases to be formed in the composition in question. It is possible to reduce the amount of martensitic phase formed by lowering the soak temperature toward lower values in the intercritical range, or else by carrying out a slow cooling operation before the quench.
  • this tempering operation is in no case an averaging treatment, as is found in the prior art. This is because these averaging treatments, which are generally carried out between 300 and 500° C., have in particular the effect of suppressing the martensite, which is an essential element of the present invention.
  • the tempering optionally carried out according to the invention consists in precipitating some of the carbon in solid solution trapped in the martensite, without reducing the proportion of this martensite.
  • the maximum temperature of this tempering operation is 300° C., preferably 250° C. and more particularly preferably 200° C.
  • composition according to the invention includes carbon with a content of between 0.010% and 0.100%. This element is essential for obtaining good mechanical properties but it must not be present in too great an amount, as it would cause an excessive proportion of martensitic phase to be formed.
  • Manganese with a content of between 0.050% and 1.0%. Manganese improves the yield strength of the steel, but greatly reduces its ductility. This is why its content is limited.
  • the composition also includes chromium with a content of between 0.010% and 1.0%, which helps in the desired martensite formation.
  • the composition also includes silicon with a content of between 0.010% and 0.50%. This greatly improves the yield strength of the steel, but slightly reduces its ductility and degrades its coatability.
  • the composition also includes phosphorus with a content of between 0.001% and 0.20%, which hardens the microstructure without affecting its texture.
  • the composition also includes aluminum with a content of between 0.010% and 0.10%, which prevents aging by nitrogen trapping.
  • the balance of the compositions consists of iron and inevitable impurities resulting from the smelting.
  • the two grades were austenized at 1250° C. for one hour, so as to dissolve the aluminum nitrides.
  • the slabs were then hot rolled in such a way that the end-of-rolling temperature was above 900° C., the value of AR 3 for both grades being about 870° C.
  • the hot-rolled strips were then cooled by water quenching, at a cooling rate of around 25° C./s, until the coiling temperature was reached.
  • Grade A was coiled at 720° C.
  • one specimen of grade B was coiled at 550° C. and another at 720 ° C.
  • the various specimens were then cold rolled so as to achieve a reduction ratio of 75%, then they underwent an annealing treatment at a soak temperature of 750° C. in the case of some specimens and 800° C. in the case of the others.
  • the cooling down to the ambient temperature was then carried out at a rate of around 25° C./s by water quenching.
  • FIG. 1 shows the relationship between the mean coefficient r and the content of martensite formed %m for grades A and B. It may be seen that the higher the martensite content, the more anisotropic the steel.
  • FIG. 2 shows the microstructure obtained with grade A, coiled at 720° C. and then annealed at 750° C. in order finally to obtain 12% martensite.
  • the ferrite and the martensite formed can be clearly distinguished in the figure.

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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)
US10/544,206 2003-02-05 2004-01-30 Method of producing a cold-rolled band of dual-phase steel with a ferritic/martensitic structure and band thus obtained Abandoned US20060144482A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
FR03/01358 2003-02-05
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
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

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US20060144482A1 true US20060144482A1 (en) 2006-07-06

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US10/544,206 Abandoned US20060144482A1 (en) 2003-02-05 2004-01-30 Method of producing a cold-rolled band of dual-phase steel with a ferritic/martensitic structure and band thus obtained

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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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US20080289726A1 (en) * 2004-11-24 2008-11-27 Nucor Corporation Cold rolled, dual phase, steel sheet and method of manufacturing same
US20090071574A1 (en) * 2004-11-24 2009-03-19 Nucor Corporation Cold rolled dual phase steel sheet having high formability and method of making the same
US20090071575A1 (en) * 2004-11-24 2009-03-19 Nucor Corporation Hot rolled dual phase steel sheet, and method of making the same
US20090098408A1 (en) * 2007-10-10 2009-04-16 Nucor Corporation Complex metallographic structured steel and method of manufacturing same
US20100043925A1 (en) * 2006-09-27 2010-02-25 Nucor Corporation High strength, hot dip coated, dual phase, steel sheet and method of manufacturing same
WO2014145536A1 (en) * 2013-03-15 2014-09-18 Am/Ns Calvert Llc New high strength bake hardenable low alloy steel and process for manufacture thereof
US20160245367A1 (en) * 2013-12-04 2016-08-25 Schaeffler Technologies AG & Co. KG Chain element
US10378077B2 (en) 2014-07-03 2019-08-13 Arcelormittal Method for producing an ultra high strength coated or not coated steel sheet and obtained sheet
US10612113B2 (en) * 2013-07-30 2020-04-07 Salzgitter Flachstahl Gmbh Micro-alloyed high-strength multi-phase steel containing silicon and having a minimum tensile strength of 750 MPA and improved properties and method for producing a strip from said steel
US11035020B2 (en) 2015-12-29 2021-06-15 Arcelormittal Galvannealed steel sheet
US11155902B2 (en) 2006-09-27 2021-10-26 Nucor Corporation High strength, hot dip coated, dual phase, steel sheet and method of manufacturing same
US11198928B2 (en) 2011-11-28 2021-12-14 Arcelormittal Method for producing high silicon dual phase steels with improved ductility
US11827948B2 (en) 2015-12-21 2023-11-28 Arcelormittal Method for producing a high strength coated steel sheet having improved ductility and formability, and obtained coated steel sheet
US12084738B2 (en) 2015-12-21 2024-09-10 Arcelormittal Method for producing a steel sheet having improved strength, ductility and formability

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CN101768697B (zh) * 2008-12-31 2012-09-19 宝山钢铁股份有限公司 用一次冷轧法生产取向硅钢的方法
CN101781739A (zh) * 2010-03-18 2010-07-21 武汉钢铁(集团)公司 抗拉强度500MPa级汽车用冷轧双相钢
CN102115808B (zh) * 2010-11-17 2013-04-24 山东钢铁股份有限公司 铁素体区轧制温度控制系统
CN103459619B (zh) * 2011-03-22 2015-06-10 日立金属株式会社 热轧马氏体时效钢带的卷绕方法
RU2563397C2 (ru) * 2011-07-06 2015-09-20 Ниппон Стил Энд Сумитомо Метал Корпорейшн Способ получения холоднокатаного стального листа
JP2013181183A (ja) * 2012-02-29 2013-09-12 Jfe Steel Corp 降伏強度の面内異方性の小さい高強度冷延鋼板およびその製造方法
RU2587102C1 (ru) * 2012-04-23 2016-06-10 ДжФЕ СТИЛ КОРПОРЕЙШН Высокопрочный стальной лист и способ его изготовления
RU2491357C1 (ru) * 2012-05-10 2013-08-27 Федеральное государственное автономное образовательное учреждение высшего профессионального образования "Национальный исследовательский технологический университет "МИСиС" Способ производства листовой стали
CN102703815A (zh) * 2012-06-19 2012-10-03 东北大学 一种600MPa级热轧双相钢及其制备方法
WO2014081779A1 (en) * 2012-11-20 2014-05-30 Thyssenkrupp Steel Usa, Llc Process for manufacturing ferritic hot rolled steel strip
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US9790567B2 (en) 2012-11-20 2017-10-17 Thyssenkrupp Steel Usa, Llc Process for making coated cold-rolled dual phase steel sheet
RU2529323C1 (ru) * 2013-06-27 2014-09-27 Открытое акционерное общество "Северсталь" (ОАО "Северсталь") Способ производства оцинкованной полосы для последующего нанесения полимерного покрытия
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WO2016118945A1 (en) * 2015-01-23 2016-07-28 Alcoa Inc. Aluminum alloy products
US10808293B2 (en) 2015-07-15 2020-10-20 Ak Steel Properties, Inc. High formability dual phase steel
CN105401071B (zh) * 2015-12-22 2017-12-29 武汉钢铁有限公司 一种500MPa级轿车用镀锌双相钢及生产方法
RU2718604C1 (ru) * 2019-11-05 2020-04-08 Публичное акционерное общество "Магнитогорский металлургический комбинат" Способ производства холоднокатаного высокопрочного проката различных классов прочности из двухфазной ферритно-мартенситной стали

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Cited By (26)

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US20080289726A1 (en) * 2004-11-24 2008-11-27 Nucor Corporation Cold rolled, dual phase, steel sheet and method of manufacturing same
US20090071574A1 (en) * 2004-11-24 2009-03-19 Nucor Corporation Cold rolled dual phase steel sheet having high formability and method of making the same
US20090071575A1 (en) * 2004-11-24 2009-03-19 Nucor Corporation Hot rolled dual phase steel sheet, and method of making the same
US7879160B2 (en) 2004-11-24 2011-02-01 Nucor Corporation Cold rolled dual-phase steel sheet
US7959747B2 (en) 2004-11-24 2011-06-14 Nucor Corporation Method of making cold rolled dual phase steel sheet
US8337643B2 (en) 2004-11-24 2012-12-25 Nucor Corporation Hot rolled dual phase steel sheet
US8366844B2 (en) 2004-11-24 2013-02-05 Nucor Corporation Method of making hot rolled dual phase steel sheet
US11155902B2 (en) 2006-09-27 2021-10-26 Nucor Corporation High strength, hot dip coated, dual phase, steel sheet and method of manufacturing same
US20100043925A1 (en) * 2006-09-27 2010-02-25 Nucor Corporation High strength, hot dip coated, dual phase, steel sheet and method of manufacturing same
US20090098408A1 (en) * 2007-10-10 2009-04-16 Nucor Corporation Complex metallographic structured steel and method of manufacturing same
US9157138B2 (en) 2007-10-10 2015-10-13 Nucor Corporation Complex metallographic structured high strength steel and method of manufacturing
US8435363B2 (en) 2007-10-10 2013-05-07 Nucor Corporation Complex metallographic structured high strength steel and manufacturing same
US11198928B2 (en) 2011-11-28 2021-12-14 Arcelormittal Method for producing high silicon dual phase steels with improved ductility
WO2014145536A1 (en) * 2013-03-15 2014-09-18 Am/Ns Calvert Llc New high strength bake hardenable low alloy steel and process for manufacture thereof
US10612113B2 (en) * 2013-07-30 2020-04-07 Salzgitter Flachstahl Gmbh Micro-alloyed high-strength multi-phase steel containing silicon and having a minimum tensile strength of 750 MPA and improved properties and method for producing a strip from said steel
US20160245367A1 (en) * 2013-12-04 2016-08-25 Schaeffler Technologies AG & Co. KG Chain element
US11035436B2 (en) * 2013-12-04 2021-06-15 Schaeffler Technologies AG & Co. KG Chain element
US11124853B2 (en) 2014-07-03 2021-09-21 Arcelormittal Method for producing a ultra high strength coated or not coated steel sheet and obtained sheet
US11131003B2 (en) 2014-07-03 2021-09-28 Arcelormittal Method for producing an ultra high strength coated or not coated steel sheet and obtained sheet
US11001904B2 (en) 2014-07-03 2021-05-11 Arcelormittal Method for producing an ultra high strength coated or not coated steel sheet and obtained sheet
US10378077B2 (en) 2014-07-03 2019-08-13 Arcelormittal Method for producing an ultra high strength coated or not coated steel sheet and obtained sheet
US12157922B2 (en) 2014-07-03 2024-12-03 Arcelormittal Method for producing a ultra high strength coated or not coated steel sheet and obtained sheet
US11827948B2 (en) 2015-12-21 2023-11-28 Arcelormittal Method for producing a high strength coated steel sheet having improved ductility and formability, and obtained coated steel sheet
US12084738B2 (en) 2015-12-21 2024-09-10 Arcelormittal Method for producing a steel sheet having improved strength, ductility and formability
US11035020B2 (en) 2015-12-29 2021-06-15 Arcelormittal Galvannealed steel sheet
US11512362B2 (en) 2015-12-29 2022-11-29 Arcelormittal Method for producing an ultra high strength galvannealed steel sheet and obtained galvannealed steel sheet

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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
CA2514736C (fr) 2012-12-04
PL377834A1 (pl) 2006-02-20
JP4528769B2 (ja) 2010-08-18
EP1592816B1 (fr) 2020-10-14
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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