EP1587963B1 - Ultrahigh strength hot-rolled steel and method of producing bands - Google Patents
Ultrahigh strength hot-rolled steel and method of producing bands Download PDFInfo
- Publication number
- EP1587963B1 EP1587963B1 EP04701978A EP04701978A EP1587963B1 EP 1587963 B1 EP1587963 B1 EP 1587963B1 EP 04701978 A EP04701978 A EP 04701978A EP 04701978 A EP04701978 A EP 04701978A EP 1587963 B1 EP1587963 B1 EP 1587963B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- steel
- hot
- iron
- strength
- ferrite
- 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
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 46
- 239000010959 steel Substances 0.000 title claims abstract description 46
- 238000000034 method Methods 0.000 title claims description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 22
- 239000000203 mixture Substances 0.000 claims abstract description 20
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 13
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 11
- 229910052742 iron Inorganic materials 0.000 claims abstract description 11
- 238000004519 manufacturing process Methods 0.000 claims abstract description 9
- 239000000126 substance Substances 0.000 claims abstract description 4
- 238000001816 cooling Methods 0.000 claims description 12
- 229910052698 phosphorus Inorganic materials 0.000 claims description 10
- 229910052782 aluminium Inorganic materials 0.000 claims description 6
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 5
- 229910001297 Zn alloy Inorganic materials 0.000 claims description 5
- 238000005096 rolling process Methods 0.000 claims description 5
- 239000011701 zinc Substances 0.000 claims description 5
- 229910052725 zinc Inorganic materials 0.000 claims description 5
- 229910001563 bainite Inorganic materials 0.000 claims description 4
- 238000003723 Smelting Methods 0.000 claims 4
- 238000007598 dipping method Methods 0.000 claims 1
- 238000004804 winding Methods 0.000 description 9
- 239000011651 chromium Substances 0.000 description 7
- 239000010936 titanium Substances 0.000 description 7
- 229910052799 carbon Inorganic materials 0.000 description 4
- 239000011572 manganese Substances 0.000 description 4
- 238000007493 shaping process Methods 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 229910000611 Zinc aluminium Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000001914 calming effect Effects 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000007596 consolidation process Methods 0.000 description 1
- 230000000593 degrading effect Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000003618 dip coating Methods 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 230000000930 thermomechanical effect Effects 0.000 description 1
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
- 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
- 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
- C21D8/0226—Hot rolling
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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
- C21D2211/002—Bainite
-
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot 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
- 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
- the present invention relates to a hot-rolled steel with a very high strength, and a method of manufacturing strips of this steel, whose structure is bainito-martensitic and can contain up to 5% of ferrite.
- 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 the reduction of weight and thus the thickness of parts, and the improvement of safety. which goes through the increase of the resistance to fatigue and the shock resistance of the parts. These improvements should not further deteriorate the fitness of the sheets used in the manufacture of parts.
- Improved impact resistance of shaped parts can be achieved in different ways and, in particular, by using steels having on the one hand a significant elongation A and on the other hand an E / Rm ratio having a low value, which allows after shaping and thanks to the consolidation capacity of the steel to increase its elastic limit.
- the fatigue life of the parts defines their service life according to the stresses undergone, and can be improved by increasing the tensile strength Rm of the steel. But, the increase in strength deteriorates the ability to shape the steel, thus limiting the workable parts, particularly with regard to their thickness.
- high-strength steel denotes a steel whose tensile strength Rm is greater than 800 MPa.
- a second family of very high strength steels consists of so-called dual phase steels with a structure comprising approximately 10% ferrite and 90% martensite. These steels have a very good formability, but resistance levels not exceeding 800 MPa.
- US6364968 discloses a method for producing a very high strength hot rolled steel sheet which comprises preparing and heating a slab of composition 0.05% ⁇ C ⁇ 0.3%, 1.5% ⁇ Mn ⁇ 3, 5%, 0.03% ⁇ S ⁇ 1%, Al ⁇ 0.07%, S ⁇ 0.05%, P ⁇ 0.02%, N ⁇ 0.0200%, 0.003% ⁇ Nb ⁇ 0.20% or / and 0.005% ⁇ Si ⁇ 0.20% remains iron and impurities resulting from processing at a temperature ⁇ 1200 ° C, hot rolling at a temperature> 800 ° C, cooling this sheet with a cooling rate of 20-150 ° C and winding said sheet at a winding temperature of 300-350 ° C and a steel having this composition.
- the object of the present invention is to overcome the drawbacks of the steels of the prior art by providing a hot rolled steel with very high strength, suitable for shaping, and having improved fatigue strength and impact resistance.
- the invention firstly relates to a hot rolled steel with very high strength, characterized in that its chemical composition comprises, by weight: 0 , 05 % ⁇ VS ⁇ 0 , 1 % 0 , 7 % ⁇ mn ⁇ 1 , 1 % 0 , 5 % ⁇ Cr ⁇ 1 , 0 % 0 , 05 % ⁇ Yes ⁇ 0 , 3 % 0 , 05 % ⁇ Ti ⁇ 0 , 1 % al ⁇ 0 , 07 % S ⁇ 0 , 03 % P ⁇ 0 , 05 % the rest being iron and impurities resulting from the elaboration, said steel having a bainito-martensitic structure which can contain up to 5% of ferrite.
- the chemical composition further comprises, by weight: 0 , 08 % ⁇ VS ⁇ 0 , 09 % 0 , 8 % ⁇ mn ⁇ 1 , 0 % 0 , 6 % ⁇ Cr ⁇ 0 , 9 % 0 , 2 % ⁇ Yes ⁇ 0 , 3 % 0 , 05 % ⁇ Ti ⁇ 0 , 09 % al ⁇ 0 , 07 % S ⁇ 0 , 03 % P ⁇ 0 , 05 % . the rest being iron and impurities resulting from the elaboration.
- the structure of the steel according to the invention consists of 70 to 90% of bainite, 10 to 30% of martensite and 0 to 5% of ferrite, and more particularly preferably from 70 to 85% of bainite, from 15 to 30% of martensite and from 0 to 5% of ferrite.
- the subject of the invention is also a method for producing a very high-strength hot-rolled steel strip according to the invention, in which a slab is hot-rolled, the composition of which comprises: 0 , 05 % ⁇ VS ⁇ 0 , 1 % 0 , 7 % ⁇ mn ⁇ 1 , 1 % 0 , 5 % ⁇ Cr ⁇ 1 , 0 % 0 , 05 % ⁇ Yes ⁇ 0 , 3 % 0 , 05 % ⁇ Ti ⁇ 0 , 1 % al ⁇ 0 , 07 % S ⁇ 0 , 03 % P ⁇ 0 , 05 % the rest being iron and impurities resulting from the elaboration, the rolling temperature being below 950 ° C., and the strip thus obtained is cooled to a temperature of less than or equal to 400 ° C., while maintaining a cooling rate greater than 50 ° C./s between 800 and 700 ° C.
- the composition of the slab is as follows: 0 , 08 % ⁇ VS ⁇ 0 , 09 % 0 , 8 % ⁇ mn ⁇ 1 , 0 % 0 , 6 % ⁇ Cr ⁇ 0 , 9 % 0 , 2 % ⁇ Yes ⁇ 0 , 3 % 0 , 05 % ⁇ Ti ⁇ 0 , 09 % al ⁇ 0 , 07 % S ⁇ 0 , 03 % P ⁇ 0 , 05 % the rest being iron and impurities resulting from the elaboration.
- the hot-rolled steel strip is coated with zinc or a zinc alloy, by immersion in a bath of zinc or molten zinc alloy, after winding and after being unreeled, then annealed.
- the method according to the invention consists first of all in hot rolling a slab of specific composition, in order to obtain a homogeneous structure.
- the rolling temperature is less than 950 ° C, and preferably less than 900 ° C.
- the strip thus obtained is cooled to a temperature of less than or equal to 400 ° C., while maintaining a cooling rate greater than 50 ° C./s between 800 and 700 ° C.
- This rapid cooling is carried out in such a way that less than 5% of ferrite, which is not desired, is formed because the titanium would precipitate preferentially in this phase.
- This cooling rate is preferably between 50 ° C / s and 200 ° C / s.
- the method then consists in winding the strip at a winding temperature of less than or equal to 250 ° C.
- We limit the temperature of this stage in order to avoid generating an income from martensite, which would reduce the mechanical strength and raise the elastic limit, resulting in a bad E / Rm ratio.
- composition according to the invention comprises carbon with a content of between 0.05% and 0.100%.
- This element is essential for obtaining good mechanical characteristics, but must not be present in too large quantities, because it could generate segregations.
- a carbon content of less than 0.100 makes it possible in particular to have good weldability, and to improve the shaping properties and the endurance limit.
- Manganese at a level of between 0.7% and 1.1%. Manganese improves the yield strength of steel while greatly reducing its ductility, for which it limits its content. A content of less than 1.1% also prevents segregation during continuous casting.
- the composition also comprises chromium at a level of between 0.50% and 1.0%.
- a minimum content of 0.50% makes it possible to promote the appearance of bainite in the microstructure. However, its content is limited to 1.0% because a high chromium content would favor the increase of the amount of ferrite formed above 5%, because of its alphagenic character.
- the composition also comprises silicon at a content of between 0.05% and 0.3%. It greatly improves the yield strength of steel while reducing its ductility slightly and deteriorating its coating, which is why its content is limited.
- the composition also comprises titanium at a content of between 0.05 and 0.1%.
- This element makes it possible to significantly increase the mechanical characteristics by a phenomenon of precipitation during rolling and cooling. It does not increase the hot hardness because of its moderate content. Its content is limited to 0.1% in order to avoid degrading the impact resistance properties, the hot hardness and the folding ability.
- composition may also comprise phosphorus at a content of less than 0.05%, since, beyond that, it could pose problems of segregation during continuous casting.
- the composition also comprises aluminum with a content of less than 0.07%, which occurs during the calming of the steel during its manufacture at the steel mill.
- a steel grade has been developed. Its composition is given in the following table: VS mn Cr Yes Ti S P al AT 0.78 0.95 0.79 0.233 0.094 0,001 0,038 0.048 The rest of the composition consists of iron and unavoidable impurities resulting from the elaboration.
- microstructure of test 1 is bainito-martensitic, whereas the microstructure of tests 2 and 3 is ferritic-bainitic.
- a winding temperature greater than 250 ° C. associated with a cooling rate between 800 and 700 ° C. of less than 50 ° C./s, increases the yield strength without increasing the mechanical strength.
- the ratio E / Rm is therefore too high.
- the steel according to the invention has a good ability to dip coating in a bath of molten metal, such as zinc or a zinc alloy, or aluminum or an alloy thereof.
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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)
Abstract
Description
La présente invention concerne un acier laminé à chaud à très haute résistance, et un procédé de fabrication de bandes de cet acier, dont la structure est bainito-martensitique et peut contenir jusqu'à 5% de ferrite.The present invention relates to a hot-rolled steel with a very high strength, and a method of manufacturing strips of this steel, whose structure is bainito-martensitic and can contain up to 5% of ferrite.
Les aciers à très haute résistance ont été développés ces dernières années, notamment afin de répondre aux besoins spécifiques de l'industrie automobile, qui sont en particulier la réduction du poids et donc de l'épaisseur des pièces, et l'amélioration de la sécurité qui passe par l'augmentation de la résistance à la fatigue et de la tenue aux chocs des pièces. Ces améliorations ne doivent en outre pas détériorer l'aptitude à la mise en forme des tôles utilisées pour la fabrication des pièces.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 the reduction of weight and thus the thickness of parts, and the improvement of safety. which goes through the increase of the resistance to fatigue and the shock resistance of the parts. These improvements should not further deteriorate the fitness of the sheets used in the manufacture of parts.
Cette aptitude à la mise en forme suppose que l'acier présente un allongement A important (> 10%) ainsi qu'un rapport de la limite d'élasticité E sur la résistance à la traction Rm ayant une valeur basse.This formability assumes that the steel has a significant elongation A (> 10%) as well as a ratio of the yield strength E on the tensile strength Rm having a low value.
L'amélioration de la tenue aux chocs des pièces mises en forme peut être réalisée de différentes façons et, en particulier, en utilisant des aciers possédant d'une part un allongement A important et, d'autre part, un rapport E/Rm ayant une valeur basse, ce qui permet après mise en forme et grâce à la capacité de consolidation de l'acier d'augmenter sa limite d'élasticité.Improved impact resistance of shaped parts can be achieved in different ways and, in particular, by using steels having on the one hand a significant elongation A and on the other hand an E / Rm ratio having a low value, which allows after shaping and thanks to the consolidation capacity of the steel to increase its elastic limit.
La tenue en fatigue des pièces définit leur durée de vie en fonction des contraintes subies, et peut être améliorée en augmentant la résistance à la traction Rm de l'acier. Mais, l'augmentation de la résistance détériore l'aptitude à la mise en forme de l'acier, limitant ainsi les pièces réalisables, en particulier en ce qui concerne leur épaisseur.The fatigue life of the parts defines their service life according to the stresses undergone, and can be improved by increasing the tensile strength Rm of the steel. But, the increase in strength deteriorates the ability to shape the steel, thus limiting the workable parts, particularly with regard to their thickness.
Par acier à très haute résistance, on désigne dans le cadre de la présente invention, un acier dont la résistance à la traction Rm est supérieure à 800 MPa.For the purposes of the present invention, the term "high-strength steel" denotes a steel whose tensile strength Rm is greater than 800 MPa.
On connaît une première famille d'aciers à très haute résistance, qui sont des aciers contenant des proportions élevées de carbone (plus de 0,1%) et de manganèse (plus de 1,2%) et dont la structure est entièrement martensitique. Ils présentent une résistance de plus de 1000 MPa, obtenue par un traitement thermique de trempe, mais ont un allongement A de moins de 8% ce qui interdit toute mise en forme.There is a first family of very high strength steels, which are steels containing high proportions of carbon (over 0.1%) and manganese (more than 1.2%) and whose structure is entirely martensitic. They have a resistance of more than 1000 MPa, obtained by a quenching heat treatment, but have an elongation A of less than 8%, which prevents any shaping.
Une deuxième famille d'aciers à très haute résistance est constituée d'aciers dits dual phase, à structure comprenant environ 10% de ferrite et 90% de martensite. Ces aciers présentent une très bonne formabilité, mais des niveaux de résistance ne dépassant pas 800 MPa.A second family of very high strength steels consists of so-called dual phase steels with a structure comprising approximately 10% ferrite and 90% martensite. These steels have a very good formability, but resistance levels not exceeding 800 MPa.
Le but de la présente invention est de remédier aux inconvénients des aciers de l'art antérieur en proposant un acier laminé à chaud à très haute résistance, apte à la mise en forme, et présentant une tenue en fatigue et une tenue aux chocs améliorées.The object of the present invention is to overcome the drawbacks of the steels of the prior art by providing a hot rolled steel with very high strength, suitable for shaping, and having improved fatigue strength and impact resistance.
A cet effet, l'invention a pour premier objet un acier laminé à chaud à très haute résistance, caractérisé en ce que sa composition chimique comprend, en poids :
le reste étant du fer et des impuretés résultant de l'élaboration,
ledit acier ayant une structure bainito-martensitique pouvant contenir jusqu'à 5% de ferrite.To this end, the invention firstly relates to a hot rolled steel with very high strength, characterized in that its chemical composition comprises, by weight:
the rest being iron and impurities resulting from the elaboration,
said steel having a bainito-martensitic structure which can contain up to 5% of ferrite.
Dans un mode de réalisation préféré, la composition chimique comprend en outre, en poids :
le reste étant du fer et des impuretés résultant de l'élaboration.In a preferred embodiment, the chemical composition further comprises, by weight:
the rest being iron and impurities resulting from the elaboration.
Dans un autre mode de réalisation préféré, la structure de l'acier selon l'invention est constituée de 70 à 90% de bainite, de 10 à 30% de martensite et de 0 à 5% de ferrite, et de façon plus particulièrement préférée, de 70 à 85% de bainite, de 15 à 30% de martensite et de 0 à 5% de ferrite.In another preferred embodiment, the structure of the steel according to the invention consists of 70 to 90% of bainite, 10 to 30% of martensite and 0 to 5% of ferrite, and more particularly preferably from 70 to 85% of bainite, from 15 to 30% of martensite and from 0 to 5% of ferrite.
L'acier selon l'invention peut également comprendre les caractéristiques suivantes, seules ou en combinaison :
- une résistance à la traction Rm supérieure ou égale à 950 MPa,
- un allongement à la rupture A supérieur ou égal à 10%,
- une limite d'élasticité E supérieure ou égale à 680 MPa,
- un rapport E/Rm inférieur à 0,8.
- a tensile strength Rm greater than or equal to 950 MPa,
- an elongation at break A greater than or equal to 10%,
- a yield strength E greater than or equal to 680 MPa,
- an E / Rm ratio of less than 0.8.
L'invention a également pour deuxième objet un procédé de fabrication d'une bande d'acier laminé à chaud à très haute résistance selon l'invention, dans lequel on lamine à chaud une brame dont la composition comprend :
le reste étant du fer et des impuretés résultant de l'élaboration,
la température de laminage étant inférieure à 950°C, puis on fait refroidir la bande ainsi obtenue jusqu'à une température inférieure ou égale à 400°C, en maintenant une vitesse de refroidissement supérieure à 50°C/s entre 800 et 700°C, puis on bobine ladite bande à une température de bobinage inférieure ou égale à 250°C.The subject of the invention is also a method for producing a very high-strength hot-rolled steel strip according to the invention, in which a slab is hot-rolled, the composition of which comprises:
the rest being iron and impurities resulting from the elaboration,
the rolling temperature being below 950 ° C., and the strip thus obtained is cooled to a temperature of less than or equal to 400 ° C., while maintaining a cooling rate greater than 50 ° C./s between 800 and 700 ° C. C, then said coil is wound at a winding temperature of less than or equal to 250 ° C.
Dans un mode de réalisation préféré, la composition de la brame est la suivante :
le reste étant du fer et des impuretés résultant de l'élaboration.In a preferred embodiment, the composition of the slab is as follows:
the rest being iron and impurities resulting from the elaboration.
Dans un autre mode de réalisation préféré, la bande d'acier laminé à chaud est revêtue de zinc ou d'un alliage de zinc, par immersion dans un bain de zinc ou d'alliage de zinc fondu, à l'issue du bobinage et après avoir été débobinée, puis recuite.In another preferred embodiment, the hot-rolled steel strip is coated with zinc or a zinc alloy, by immersion in a bath of zinc or molten zinc alloy, after winding and after being unreeled, then annealed.
Le procédé selon l'invention consiste tout d'abord à laminer à chaud une brame de composition spécifique, afin d'obtenir une structure homogène. La température de laminage est inférieure à 950°C, et de préférence inférieure à 900°C.The method according to the invention consists first of all in hot rolling a slab of specific composition, in order to obtain a homogeneous structure. The rolling temperature is less than 950 ° C, and preferably less than 900 ° C.
A l'issue du laminage, on fait refroidir la bande ainsi obtenue jusqu'à une température inférieure ou égale à 400°C, en maintenant une vitesse de refroidissement supérieure à 50°C/s entre 800 et 700°C. Ce refroidissement rapide est effectué de telle sorte que l'on forme moins de 5% de ferrite, dont on ne souhaite pas la présence, car le titane précipiterait préférentiellement dans cette phase. Cette vitesse de refroidissement est de préférence comprise entre 50°C/s et 200°C/s.At the end of rolling, the strip thus obtained is cooled to a temperature of less than or equal to 400 ° C., while maintaining a cooling rate greater than 50 ° C./s between 800 and 700 ° C. This rapid cooling is carried out in such a way that less than 5% of ferrite, which is not desired, is formed because the titanium would precipitate preferentially in this phase. This cooling rate is preferably between 50 ° C / s and 200 ° C / s.
Le procédé consiste ensuite à bobiner la bande à une température de bobinage inférieure ou égale à 250°C. On limite la température de cette étape afin d'éviter de provoquer un revenu de la martensite, qui diminuerait la résistance mécanique et ferait remonter la limite élastique, d'ou un mauvais ratio E/Rm.The method then consists in winding the strip at a winding temperature of less than or equal to 250 ° C. We limit the temperature of this stage in order to avoid generating an income from martensite, which would reduce the mechanical strength and raise the elastic limit, resulting in a bad E / Rm ratio.
La composition selon l'invention comprend du carbone à une teneur comprise entre 0,05% et 0,100%. Cet élément est essentiel à l'obtention de bonnes caractéristiques mécaniques, mais ne doit pas être présent en trop grande quantité, car il pourrait générer des ségrégations. Une teneur en carbone inférieure à 0,100 permet notamment d'avoir une bonne soudabilité, et une amélioration des propriétés de mise en forme et de limite d'endurance.The composition according to the invention comprises carbon with a content of between 0.05% and 0.100%. This element is essential for obtaining good mechanical characteristics, but must not be present in too large quantities, because it could generate segregations. A carbon content of less than 0.100 makes it possible in particular to have good weldability, and to improve the shaping properties and the endurance limit.
Elle comprend également du manganèse à une teneur comprise entre 0,7% et 1,1%. Le manganèse améliore la limite d'élasticité de l'acier tout en réduisant fortement sa ductilité, ce pour quoi on limite sa teneur. Une teneur inférieure à 1,1% permet également d'éviter toute ségrégation lors de la coulée continue.It also includes manganese at a level of between 0.7% and 1.1%. Manganese improves the yield strength of steel while greatly reducing its ductility, for which it limits its content. A content of less than 1.1% also prevents segregation during continuous casting.
La composition comprend également du chrome à une teneur comprise entre 0,50% et 1,0%. Une teneur minimale de 0,50% permet de favoriser l'apparition de la bainite dans la microstructure. On limite cependant sa teneur à 1,0% car une teneur élevée en chrome favoriserait l'augmentation de la quantité de ferrite formée au-delà de 5%, en raison de son caractère alphagène.The composition also comprises chromium at a level of between 0.50% and 1.0%. A minimum content of 0.50% makes it possible to promote the appearance of bainite in the microstructure. However, its content is limited to 1.0% because a high chromium content would favor the increase of the amount of ferrite formed above 5%, because of its alphagenic character.
La composition comprend également du silicium à une teneur comprise entre 0,05% et 0,3%. Il améliore fortement la limite d'élasticité de l'acier tout en réduisant faiblement sa ductilité et en détériorant sa revêtabilité, ce qui explique pourquoi on limite sa teneur.The composition also comprises silicon at a content of between 0.05% and 0.3%. It greatly improves the yield strength of steel while reducing its ductility slightly and deteriorating its coating, which is why its content is limited.
La composition comprend également du titane à une teneur comprise entre 0,05 et 0,1%. Cet élément permet d'accroître notablement les caractéristiques mécaniques par un phénomène de précipitation au cours du laminage et du refroidissement. Il n'augmente pas la dureté à chaud du fait de sa teneur modérée. On limite sa teneur à 0,1% pour éviter de dégrader les propriétés de résistance au choc, la dureté à chaud, ainsi que l'aptitude au pliage.The composition also comprises titanium at a content of between 0.05 and 0.1%. This element makes it possible to significantly increase the mechanical characteristics by a phenomenon of precipitation during rolling and cooling. It does not increase the hot hardness because of its moderate content. Its content is limited to 0.1% in order to avoid degrading the impact resistance properties, the hot hardness and the folding ability.
La composition peut également comprendre du phosphore à une teneur inférieure à 0,05%, car au-delà il pourrait poser des problèmes de ségrégation lors de la coulée continue.The composition may also comprise phosphorus at a content of less than 0.05%, since, beyond that, it could pose problems of segregation during continuous casting.
La composition comprend également de l'aluminium à une teneur comprise inférieure à 0,07%, qui intervient lors du calmage de l'acier lors de son élaboration à l'aciérie.The composition also comprises aluminum with a content of less than 0.07%, which occurs during the calming of the steel during its manufacture at the steel mill.
A titre d'exemple non limitatif, et afin de mieux illustrer l'invention, une nuance d'acier a été élaborée. Sa composition est donnée dans le tableau suivant :
- Rm :Rm:
- résistance à la traction en MPa,tensile strength in MPa,
- Rp0,2 :Rp0,2:
- limite d'élasticité en MPa,yield strength in MPa,
- A :AT :
- allongement, mesuré en %lengthening, measured in%
A partir de la nuance A, on a préparé trois échantillons, en les laminant à 860°C, puis en les soumettant à des chemins thermo-mécaniques différents. On a fait varier les vitesses de refroidissement entre 800 et 700°C, ainsi que la température de bobinage, afin de mettre en évidence les différences de structure obtenues.From Grade A, three samples were prepared, laminated at 860 ° C, and subjected to different thermomechanical paths. The cooling rates were varied between 800 and 700 ° C, as well as the winding temperature, in order to highlight the structural differences obtained.
On mesure ensuite les caractéristiques mécaniques des aciers obtenus. Les résultats sont rassemblés dans le tableau suivant :
La microstructure de l'essai 1, conforme à l'invention, est bainito-martensitique, tandis que la microstructure des essais 2 et 3 est ferrito-bainitique.The microstructure of test 1, according to the invention, is bainito-martensitic, whereas the microstructure of tests 2 and 3 is ferritic-bainitic.
On constate qu'une vitesse de refroidissement entre 800 et 700C inférieure à 50°C/s, induit une présence de ferrite dans une proportion supérieure à 5%. Le titane va alors précipiter dans cette ferrite, ce qui ne permet plus d'obtenir le niveau de caractéristiques mécaniques recherché, en particulier un Rm élevé.It is found that a cooling rate between 800 and 700 ° C lower than 50 ° C./s, induces a presence of ferrite in a proportion greater than 5%. The titanium will then precipitate in this ferrite, which no longer allows to obtain the desired level of mechanical characteristics, in particular a high Rm.
Par ailleurs, une température de bobinage supérieure à 250°C, associée à une vitesse de refroidissement entre 800 et 700°C inférieure à 50°C/s, augmente la limite d'élasticité sans augmenter la résistance mécanique. Le rapport E/Rm est donc trop élevé.Moreover, a winding temperature greater than 250 ° C., associated with a cooling rate between 800 and 700 ° C. of less than 50 ° C./s, increases the yield strength without increasing the mechanical strength. The ratio E / Rm is therefore too high.
Enfin, on constate qu'une vitesse de refroidissement entre 800 et 700°C supérieure à 50°C/s, associée à une température de bobinage inférieure à 250°C, donne d'excellentes valeurs de résistance mécanique et de limite d'élasticité. La structure essentiellement bainito-martensitique confère au produit un bon ratio E/Rm et un allongement supérieur à 10%.Finally, it is found that a cooling rate between 800 and 700 ° C higher than 50 ° C / s, associated with a winding temperature of less than 250 ° C, gives excellent values of mechanical strength and yield strength. . The essentially bainitomensitic structure gives the product a good ratio E / Rm and an elongation greater than 10%.
En outre, l'acier selon l'invention présente une bonne aptitude au revêtement par immersion dans un bain de métal fondu, tel que du zinc ou un alliage de zinc, ou que de l'aluminium ou un de ses alliages.In addition, the steel according to the invention has a good ability to dip coating in a bath of molten metal, such as zinc or a zinc alloy, or aluminum or an alloy thereof.
Claims (10)
- Steel according to either of Claims 1 and 2, characterized furthermore in that its structure consists of 70 to 90% bainite, 10 to 30% martensite and 0 to 5% ferrite.
- Steel according to any one of Claims 1 to 3, characterized in that it has a tensile strength Rm of 950 MPa or higher.
- Steel according to any one of Claims 1 to 4, characterized in that it has an elongation at break A of 10% or higher.
- Steel according to any one of Claims 1 to 5, characterized in that it has a yield strength E of 680 MPa or higher.
- Steel according to any one of Claims 1 to 6, characterized in that it has an E/Rm ratio of less than 0.8.
- Process for manufacturing a strip of ultrahigh-strength hot-rolled steel according to any one of Claims 1 to 7, characterized in that a slab, whose composition comprises:
the balance being iron and impurities resulting from the smelting, is hot-rolled, the rolling temperature being below 950°C, then the strip thus obtained is cooled down to a temperature of 400°C or below, maintaining a cooling rate of greater than 50°C/s between 800 and 700°C, and then said strip is coiled at a coiling temperature of 250°C or below. - Manufacturing process according to either of Claims 8 and 9, characterized in that the hot-rolled steel strip is coated with zinc or a zinc alloy, by dipping it into a bath of molten zinc or zinc alloy following said coiling operation and after having been uncoiled, and then annealed.
Applications Claiming Priority (3)
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FR0300371 | 2003-01-15 | ||
FR0300371A FR2849864B1 (en) | 2003-01-15 | 2003-01-15 | VERY HIGH STRENGTH HOT-ROLLED STEEL AND METHOD OF MANUFACTURING STRIPS |
PCT/FR2004/000058 WO2004070064A2 (en) | 2003-01-15 | 2004-01-14 | Ultrahigh strength hot-rolled steel and method of producing bands |
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EP1587963B1 true EP1587963B1 (en) | 2011-10-12 |
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US (1) | US7699947B2 (en) |
EP (1) | EP1587963B1 (en) |
JP (1) | JP4505055B2 (en) |
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AT (1) | ATE528414T1 (en) |
BR (1) | BRPI0406731B1 (en) |
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ES (1) | ES2374188T3 (en) |
FR (1) | FR2849864B1 (en) |
MX (1) | MXPA05007580A (en) |
PL (1) | PL209154B1 (en) |
RU (1) | RU2333284C2 (en) |
UA (1) | UA79531C2 (en) |
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WO2012053044A1 (en) * | 2010-10-18 | 2012-04-26 | 住友金属工業株式会社 | Hot-rolled steel sheet, cold-rolled steel sheet, and plated steel sheet each having exellent uniform ductility and local ductility in high-speed deformation |
WO2012153008A1 (en) | 2011-05-12 | 2012-11-15 | Arcelormittal Investigación Y Desarrollo Sl | Method for the production of very-high-strength martensitic steel and sheet or part thus obtained |
WO2012153009A1 (en) * | 2011-05-12 | 2012-11-15 | Arcelormittal Investigación Y Desarrollo Sl | Method for the production of very-high-strength martensitic steel and sheet thus obtained |
CN102560272B (en) * | 2011-11-25 | 2014-01-22 | 宝山钢铁股份有限公司 | Ultrahigh-strength abrasion-resistant steel plate and manufacturing method thereof |
CA2880063C (en) * | 2012-08-03 | 2017-03-14 | Tata Steel Ijmuiden B.V. | A process for producing hot-rolled steel strip and a steel strip produced therewith |
CN103695762B (en) * | 2013-12-13 | 2016-06-08 | 安徽工业大学 | A kind of tensile strength 560��590MPa hot rolled wheel rim steel and manufacture method thereof |
PL3097214T3 (en) * | 2014-01-24 | 2021-07-05 | Rautaruukki Oyj | Hot-rolled ultrahigh strength steel strip product |
DE102017130237A1 (en) | 2017-12-15 | 2019-06-19 | Salzgitter Flachstahl Gmbh | High strength hot rolled flat steel product with high edge crack resistance and high bake hardening potential, a process for producing such a flat steel product |
KR102020435B1 (en) | 2017-12-22 | 2019-09-10 | 주식회사 포스코 | High strength hot-rolled steel sheet having excellent bendability and low-temperature toughness and mathod for manufacturing thereof |
CN115386783B (en) * | 2022-08-29 | 2023-10-03 | 东北大学 | Ultrahigh-strength steel plate with yield strength of 1000MPa and preparation method thereof |
CN115354237B (en) * | 2022-08-29 | 2023-11-14 | 东北大学 | Hot-rolled ultrahigh-strength steel plate with tensile strength of 1000MPa and preparation method thereof |
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DE2133744B2 (en) * | 1971-07-07 | 1973-07-12 | August Thyssen-Hütte AG, 4100 Duisburg | THE USE OF A FULLY KILLED STEEL FOR ARTICLES FROM HOT-ROLLED STRIP |
JPS56150135A (en) * | 1980-01-18 | 1981-11-20 | British Steel Corp | Binary steel |
US4388122A (en) * | 1980-08-11 | 1983-06-14 | Kabushiki Kaisha Kobe Seiko Sho | Method of making high strength hot rolled steel sheet having excellent flash butt weldability, fatigue characteristic and formability |
US4501626A (en) * | 1980-10-17 | 1985-02-26 | Kabushiki Kaisha Kobe Seiko Sho | High strength steel plate and method for manufacturing same |
US4472208A (en) * | 1982-06-28 | 1984-09-18 | Sumitomo Metal Industries, Ltd. | Hot-rolled high tensile titanium steel plates and production thereof |
JP2819344B2 (en) * | 1990-05-11 | 1998-10-30 | トーア・スチール株式会社 | Spring steel wire |
JPH06240356A (en) * | 1993-02-10 | 1994-08-30 | Sumitomo Metal Ind Ltd | Production of high strength hot rolled steel plate excellent in workability |
JP3425837B2 (en) * | 1996-03-28 | 2003-07-14 | 株式会社神戸製鋼所 | High-strength hot-rolled steel sheet, high-strength galvanized steel sheet excellent in pitting corrosion resistance and crushing properties, and methods for producing them |
AU736035B2 (en) * | 1997-07-28 | 2001-07-26 | Exxonmobil Upstream Research Company | Ultra-high strength, weldable steels with excellent ultra-low temperature toughness |
JPH11199984A (en) * | 1998-01-09 | 1999-07-27 | Kobe Steel Ltd | High strength steel sheet excellent in gas cutting |
FR2796966B1 (en) * | 1999-07-30 | 2001-09-21 | Ugine Sa | PROCESS FOR THE MANUFACTURE OF THIN STRIP OF TRIP-TYPE STEEL AND THIN STRIP THUS OBTAINED |
CN1107122C (en) * | 2000-02-29 | 2003-04-30 | 济南济钢设计院 | Austenic-bainite Malleable steel and its preparation |
US6364968B1 (en) * | 2000-06-02 | 2002-04-02 | Kawasaki Steel Corporation | High-strength hot-rolled steel sheet having excellent stretch flangeability, and method of producing the same |
JP4608739B2 (en) * | 2000-06-14 | 2011-01-12 | Jfeスチール株式会社 | Manufacturing method of steel pipe for automobile door reinforcement |
FR2820150B1 (en) * | 2001-01-26 | 2003-03-28 | Usinor | HIGH STRENGTH ISOTROPIC STEEL, METHOD FOR MANUFACTURING SHEETS AND SHEETS OBTAINED |
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KR20050090458A (en) | 2005-09-13 |
PL378236A1 (en) | 2006-03-20 |
WO2004070064A2 (en) | 2004-08-19 |
ZA200505161B (en) | 2006-12-27 |
US20060207692A1 (en) | 2006-09-21 |
CA2513096A1 (en) | 2004-08-19 |
US7699947B2 (en) | 2010-04-20 |
UA79531C2 (en) | 2007-06-25 |
WO2004070064A3 (en) | 2004-09-16 |
FR2849864A1 (en) | 2004-07-16 |
KR101065781B1 (en) | 2011-09-19 |
PL209154B1 (en) | 2011-07-29 |
BRPI0406731B1 (en) | 2012-11-27 |
ES2374188T3 (en) | 2012-02-14 |
CN100366759C (en) | 2008-02-06 |
RU2333284C2 (en) | 2008-09-10 |
CN1735700A (en) | 2006-02-15 |
JP2006518009A (en) | 2006-08-03 |
FR2849864B1 (en) | 2005-02-18 |
CA2513096C (en) | 2011-03-29 |
MXPA05007580A (en) | 2005-09-21 |
BRPI0406731A (en) | 2005-12-20 |
EP1587963A2 (en) | 2005-10-26 |
ATE528414T1 (en) | 2011-10-15 |
RU2005125717A (en) | 2006-02-10 |
JP4505055B2 (en) | 2010-07-14 |
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