EP1897963A1 - Tole d'acier pour la fabrication de structures allegées et procédé de fabrication de cette tole - Google Patents

Tole d'acier pour la fabrication de structures allegées et procédé de fabrication de cette tole Download PDF

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Publication number
EP1897963A1
EP1897963A1 EP06291413A EP06291413A EP1897963A1 EP 1897963 A1 EP1897963 A1 EP 1897963A1 EP 06291413 A EP06291413 A EP 06291413A EP 06291413 A EP06291413 A EP 06291413A EP 1897963 A1 EP1897963 A1 EP 1897963A1
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EP
European Patent Office
Prior art keywords
steel
steel sheet
equal
tib
sheet according
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.)
Withdrawn
Application number
EP06291413A
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German (de)
English (en)
French (fr)
Inventor
Frédéric Bonnet
Olivier Bouaziz
Jean-Claude Chevallot
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
Original Assignee
Arcelor France SA
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Arcelor France SA filed Critical Arcelor France SA
Priority to EP06291413A priority Critical patent/EP1897963A1/fr
Priority to TR2018/02707T priority patent/TR201802707T4/tr
Priority to CN2007800330419A priority patent/CN101563476B/zh
Priority to ES07823448.1T priority patent/ES2659987T3/es
Priority to EP07823448.1A priority patent/EP2064360B1/fr
Priority to PL07823448T priority patent/PL2064360T3/pl
Priority to HUE07823448A priority patent/HUE036845T2/hu
Priority to PCT/FR2007/001401 priority patent/WO2008029011A2/fr
Priority to MX2009002411A priority patent/MX2009002411A/es
Priority to JP2009527173A priority patent/JP5298017B2/ja
Priority to BRPI0716877A priority patent/BRPI0716877B1/pt
Priority to CA2662741A priority patent/CA2662741C/fr
Priority to UAA200902135A priority patent/UA95490C2/ru
Priority to KR1020097004737A priority patent/KR20090043555A/ko
Priority to RU2009108338/02A priority patent/RU2416671C2/ru
Publication of EP1897963A1 publication Critical patent/EP1897963A1/fr
Priority to ZA2009/01377A priority patent/ZA200901377B/en
Priority to MA31679A priority patent/MA30698B1/fr
Priority to US12/823,820 priority patent/US9067260B2/en
Priority to US14/513,606 priority patent/US9718125B2/en
Priority to US15/598,951 priority patent/US10702916B2/en
Withdrawn legal-status Critical Current

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Classifications

    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium

Definitions

  • the invention relates to the manufacture of steel sheets or structural parts simultaneously combining a high modulus of elasticity E, a reduced density and a high strength.
  • the invention aims to solve the above problems, in particular the large scale and economical provision of module steels. increased elasticity by the presence of TiB 2 particles.
  • the invention aims in particular at providing a continuous casting manufacturing method which does not present any particular difficulties when casting steels.
  • the invention relates to a steel sheet whose chemical composition comprises, the contents being expressed by weight: 0.010% ⁇ C ⁇ 0.20%, 0.06% ⁇ Mn ⁇ 3%, Si ⁇ 1.5%, 0.005% ⁇ Al ⁇ 1.5%, S ⁇ 0.030%, P ⁇ 0.040%, of titanium and boron in quantities such that: 2.5% ⁇ Ti ⁇ 7.2%, (0, 45 xTi) - 0.35% ⁇ B ⁇ (0.45 xTi) + 0.70%, optionally one or more elements chosen from: Ni ⁇ 1%, Mo ⁇ 1%, Cr ⁇ 3%, Nb ⁇ 0, 1%, V ⁇ 0.1%, the remainder of the composition consisting of iron and unavoidable impurities resulting from the preparation.
  • the titanium and boron contents are such that: -0.22 ⁇ B - (0.45 ⁇ Ti) ⁇ 0.35.
  • the contents of titanium and boron, expressed as% by weight, are such that: -0.35 ⁇ B - (0.45 ⁇ Ti) - 0.22.
  • the titanium content is preferably such that: 4.6% ⁇ Ti ⁇ 6.9%.
  • the titanium content is such that: 4.6% ⁇ Ti ⁇ 6%.
  • the carbon content is preferably such that: C ⁇ 0.080%.
  • the carbon content satisfies: C ⁇ 0.050%.
  • the chromium content is preferably such that: Cr ⁇ 0.08%.
  • the invention also relates to a steel sheet of the above composition, comprising eutectic precipitates of TiB 2 and optionally Fe 2 B, whose average size is less than or equal to 15 microns, and preferably less than or equal to 10 micrometers
  • more than 80% by number of TiB 2 precipitates have a monocrystalline character.
  • the invention also relates to a steel sheet according to the above characteristics, whose average grain size is less than or equal to 15 microns, preferably less than or equal to 5 microns.
  • the invention also relates to a steel sheet according to one of the above characteristics, whose modulus of elasticity measured in the rolling direction is greater than or equal to 230GPa, preferably greater than or equal to 240GPa, or preferentially greater than or equal to 250GPa
  • the strength of the steel sheet is greater than or equal to 500 MPa and its uniform elongation is greater than or equal to 8%.
  • the subject of the invention is also an article manufactured from a plurality of steel parts, of identical or different composition, of identical or different thickness, at least one of the steel parts being a steel sheet. according to any one of the above features, welded to at least one of the other parts of this object.
  • the invention also relates to a method according to which a steel is supplied according to any one of the above compositions, and the steel is cast as a semi-finished product.
  • the semi-finished product is cast as slabs or thin products between counter-rotating rolls.
  • the casting temperature does not exceed the liquidus temperature of the steel by more than 40.degree.
  • the cooling rate during the solidification of the casting is preferably greater than or equal to 0.1 ° C./s.
  • the semi-finished product is thermally rolled, optionally cold rolling and annealing, the rolling and annealing conditions being adjusted so that a steel sheet whose size is obtained is obtained.
  • grain average is less than or equal to 15 micrometers, preferably less than or equal to 5 micrometers:
  • At least one blank is cut from a steel sheet or an object according to one of the above modes, or manufactured according to one of the above modes, and the the blank is deformed into a range of temperature ranging from 20 ° to 900 ° C.
  • the invention also relates to a manufacturing method according to which one welds at least one steel sheet according to one of the above modes, or a steel sheet manufactured according to one of the modes above.
  • the invention also relates to the use of a steel sheet according to one of the above modes, or manufactured according to one of the above modes, for the manufacture of structural parts or elements reinforcement in the automotive field.
  • Carbon content is limited due to weldability: cold cracking resistance and heat-affected Zone tenacity decrease when the C content is greater than 0.20%.
  • the resistance weldability is particularly improved.
  • the carbon content is preferably limited in order to avoid a primary precipitation of TiC and / or Ti (C, N) in the liquid metal. These precipitates which form in the liquid are detrimental to the flowability in the continuous casting process of the liquid steel. On the other hand, when this precipitation occurs in the solidification or solid phase interval, it has a favorable effect on the structural hardening.
  • the maximum carbon content must therefore preferably be limited to 0.080% so as to reveal the TiC and / or Ti (C, N) precipitates, mainly during the eutectic or solid phase solidification.
  • manganese increases the quenchability, contributes to hardening in solid solution and thus to obtaining increased strength. It combines with any sulfur present, reducing the risk of hot cracking. However, beyond a content of 3% by weight of manganese, the risk of formation of a harmful band structure that would result from an eventual segregation of the manganese during solidification is increased.
  • Silicon effectively contributes to increasing strength through solid solution hardening.
  • an excessive addition of silicon causes the formation of adherent oxides that are difficult to remove during a stripping operation, and the possible appearance of surface defects due in particular to a lack of wettability in the dip galvanizing operations.
  • the silicon content should not exceed 1.5% by weight.
  • aluminum is a very effective element for the deoxidation of steel. Beyond a content of 1.5% by weight, excessive primary precipitation of alumina occurs, however, causing flowability problems.
  • Phosphorus is a known element to segregate at grain boundaries. Its content must not exceed 0.040% so as to maintain a sufficient hot ductility by avoiding the creasability and to avoid hot cracking during welding.
  • nickel or molybdenum can be added to increase the strength of the steel. For economic reasons, these additions are limited to 1% by weight.
  • chromium can be added to increase the strength. It also makes it possible to precipitate borides in a larger quantity. However, its content is limited to 3% by weight to make a less expensive steel.
  • a chromium content of less than or equal to 0.080% will be chosen.
  • an excessive addition of Cr leads to more borides being precipitated, but these are borides of (Fe, Cr)
  • niobium and vanadium may be added in an amount less than or equal to 0.1%, so as to obtain a complementary hardening in the form of precipitation of fine carbonitrides.
  • a eutectic Fe-TiB 2 precipitation occurs during solidification.
  • the eutectic character of the precipitation confers on the microstructure formed a particular character of fineness and homogeneity that is advantageous for the mechanical properties.
  • the modulus of elasticity of the steel measured in the rolling direction may exceed about 220 GPa.
  • the module can exceed 240 GPa approximately which allows to design structures with significant relief. This amount can be increased to 15% by volume to exceed about 250 GPa, especially in the case of steels comprising alloying elements such as chromium or molybdenum. The presence of these elements increases the maximum amount of TiB 2 that can be obtained in the case of eutectic precipitation.
  • the boron and titanium contents according to the invention make it possible to avoid a coarse primary precipitation of TiB 2 in the liquid metal.
  • the formation of these primary precipitates of sometimes large size (several tens of micrometers) must be avoided because of their harmful role vis-à-vis mechanisms of damage or rupture during subsequent mechanical stresses.
  • these precipitates appeared in the liquid metal, when they do not decant, are distributed in a localized manner and reduce the homogeneity of the mechanical properties. This early precipitation must be avoided because it can lead to a plugging of nozzles from the continuous casting of steel following the agglomeration of precipitates.
  • titanium must be present in sufficient quantity to lead to the endogenous formation of TiB 2 in the form of eutectic Fe-TiB 2 precipitation.
  • the titanium may also be present dissolved at room temperature in the matrix in an over-stoichiometric proportion relative to boron, calculated from TiB 2 .
  • the precipitation takes place in the form of two successive eutectics: Fe-TiB 2 in the first place, then Fe-Fe 2 B, this second endogenous Fe 2 B precipitation intervenes in greater or lesser quantity depending on the boron content of the alloy.
  • the amount precipitated as Fe 2 B can be up to 8% by volume.
  • This second precipitation also occurs according to a eutectic scheme to obtain a fine and homogeneous distribution, which ensures a good homogeneity of the mechanical characteristics.
  • Fe 2 B completes that of TiB 2 , the maximum amount of which is linked to the eutectic.
  • Fe 2 B has a role similar to that of TiB 2 . It increases the modulus of elasticity and decreases the density. It is thus possible to adjust the mechanical properties in a fine way by adjusting the precipitation complement of Fe 2 B with respect to the precipitation of TiB 2 .
  • This is a means that can be used in particular to obtain a modulus of elasticity greater than 250 GPa in steel as well as an increase in the mechanical strength of the product.
  • the modulus of elasticity increases by more than 5 GPa.
  • the elongation at break is then between 14% and 16% and the mechanical strength reaches 590 MPa.
  • the amount of Fe 2 B is greater than 7.5% by volume, the modulus of elasticity is increased by more than 10 GPa but the elongation at break is then less than 9%.
  • the average size of the eutectic precipitates of TiB 2 or Fe 2 B is less than or equal to 15 microns so as to obtain increased elongation characteristics and good fatigue properties.
  • the elongation at break may be greater than 20%.
  • the inventors have demonstrated that, when more than 80% of the number of TiB 2 eutectic precipitates have a monocrystalline character, the matrix-precipitated damage during a mechanical stress is reduced and the risk of defect formation is lower. because of the greater plasticity of the precipitate and its great cohesion with the matrix. In particular, it has been demonstrated that larger TiB 2 precipitates have hexagonal crystallization. Without wishing to be bound by theory, it is believed that this crystallographic character confers an increased possibility of deformation by twinning of these precipitates under the effect of a mechanical stress.
  • the inventors have shown that the limitation of the grain size was a very effective way to increase the mechanical characteristics of traction: When the average size grain is less than or equal to 15 micrometers, the resistance may exceed 560 MPa approximately.
  • the casting may be carried out in a format allowing the manufacture of products of various geometries, in particular the manufacture of long products.
  • the fineness of the precipitation of TiB 2 and Fe 2 B increases the strength, ductility, resilience, formability and mechanical behavior in the Heat Affected Zone.
  • the fineness of the precipitation is increased by a low casting temperature and a higher cooling rate. In particular, it has been found that a casting temperature limited to 40 ° C beyond the liquidus temperature, led to the obtaining of such fine microstructures.
  • the casting conditions will also be chosen so that the cooling rate at the time of solidification is greater than or equal to 0.1 ° C./s so that the size of the precipitates of TiB 2 and Fe 2 B is particularly fine.
  • the steel sheet thus obtained thus has a very good aptitude for shaping: without wishing to be bound by theory, it is believed that the eutectic precipitates present within a highly deformable matrix play a role similar to that played by the martensitic or bainitic phases within the ferrite in "Dual-Phase" type steels.
  • Steels according to the invention have a ratio (elasticity limit Re / resistance Rm) favorable to various shaping operations.
  • a blank is cut from the sheet and deformation is carried out by means such as stamping, folding in a range of temperature included between 20 and 900 ° C. Very good thermal stability of the TiB 2 and Fe 2 B hardening phases is observed up to 1100 ° C.
  • pieces of complex geometry with an increased modulus of elasticity can be produced according to the invention.
  • the increase of the modulus of elasticity of the steels according to the invention decreases the springback after the shaping operations and thus increases the dimensional accuracy on finished parts.
  • Structural elements are also advantageously manufactured by welding steels according to the invention of identical or different composition or thickness.
  • the melted zone given the high temperature reached, there is a partial dissolution of the precipitates and their reprecipitation cooling.
  • the amount of precipitates in the melted zone is very comparable to that of the base metal.
  • ZAC Heat Affected Zone
  • composition of a reference steel R1 containing no endogenous eutectic precipitates of TiB 2 or Fe 2 B has been indicated for comparison.
  • FIGS. 1 and 2 respectively relating to steels I-1 and I-2, shows a fine and homogeneous dispersion of endogenous TiB 2 precipitates within a ferritic matrix. Boron precipitates as a Fe-TiB 2 binary eutectic.
  • the volume amounts of precipitates were measured by means of an image analyzer and are respectively 9% and 12.4% for steels I-1 and 1-2.
  • the amount of TiB 2 in the form of primary precipitates is less than 2% by volume and promotes good flowability.
  • the average sizes of the eutectic precipitates of TiB 2 are 5 and 8 microns respectively for the I-1 and I-2 steels. Among the population of these precipitates, more than 80% in number have a monocrystalline character.
  • the semi-finished products were then hot-rolled in the form of sheets to a thickness of 3.5 mm, the end-of-rolling temperature being 940 ° C. Hot rolling was followed by winding at 700 ° C.
  • the average grain size of steel I-1 is 12 micrometers whereas it is 28 micrometers for the reference steel.
  • the modulus of elasticity of the steels I-1 and I-2 measured in the rolling direction are 230 GPa and 240 GPa, respectively.
  • the modulus of elasticity of the reference steel R-1 is 210 GPa.
  • the ratio Re / Rm of the hot-rolled or cold-rolled sheets according to the invention is close to 0.5, reflecting a mechanical behavior approaching that of a Dual-Phase steel and a good aptitude for subsequent shaping.
  • Table 4 shows the composition of three steels according to the invention.
  • Table 4 Steel compositions according to the invention (% by weight) Steel VS mn al Yes S P Ti B B- (0.45 xTi) I-3 0.0465 0.082 0.15 0.17 0.0014 0,008 5.5 2.8 0.32 I-4 0.0121 0.086 0.113 1.12 0,002 0,004 5.37 2.86 0.44 I-5 0.0154 0.084 0.1 0.885 0.0019 0,004 5.5 3.16 0.68
  • the steels were produced by casting semi-finished products, the additions of titanium and boron being carried out in the form of ferroalloys.
  • the casting temperature is 40 ° C above the liquidus temperature.
  • the steels I-3 to I-5 have an excess of boron with respect to the stoichiometry of TiB 2 so that eutectic co-precipitation of TiB 2 and Fe 2 B occur.
  • the volume amounts of eutectic precipitates are shown in Table 5.
  • Table 5 Precipitation content (% by volume) relative to I-3-4-5 steels Steel % by volume TiB 2 % by volume Fe 2 B I-3 13 3.7 I-4 12.8 5.1 I-5 13 7.9
  • FIG. 4 illustrates, in the case of steel I-3, the coexistence of TiB 2 and Fe 2 B precipitates.
  • the Fe 2 B precipitates appearing in light gray and the darker TiB 2 precipitates are dispersed. within the ferritic matrix.
  • Semi-finished steel products of composition I-2 were cast at a temperature of 1330 ° C. By varying the intensity of the cooling flow of these semi-finished products, and the thickness of the cast half-products, two cooling rates were achieved, namely 0.8 and 12 ° C / s.
  • the microstructures shown in FIGS. 6 and 7 illustrate that an increased cooling rate makes it possible to very significantly refine the eutectic Fe-TiB 2 precipitation.
  • the TiB 2 precipitates are therefore present in the various zones of the bond (base metal, ZAC, molten zone), thus the increase of the modulus of elasticity and the reduction of the density are carried out in the whole of the welded joint.
  • a 1-2 steel sheet was also welded by LASER without any difficulty in operation with a soft, stampable steel sheet whose composition contains (% by weight): 0.003% C, 0.098% Mn, 0.005% Si, 0.059% Al , 0.051% Ti, 0.0003% B, as well as unavoidable impurities resulting from the elaboration.
  • the melted zone still contains eutectic Fe-TiB 2 precipitation, in a proportion that is naturally less important than in the case of autogenous welding. In this way, it is possible to manufacture metal structures whose rigidity properties vary locally and whose mechanical characteristics correspond more specifically to the local requirements for implementation or maintenance in service
  • the invention thus allows the manufacture of structural parts or reinforcing elements with an increased level of performance, both in terms of intrinsic lightening as the increase of the modulus of elasticity.
  • the easy welding of the steel sheets according to the invention makes their incorporation possible within more complex structures, in particular by means of connections with pieces of steels of different composition or thickness. We will take particular advantage of these different characteristics in the automotive field.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
  • Laminated Bodies (AREA)
  • Continuous Casting (AREA)
  • Resistance Welding (AREA)
EP06291413A 2006-09-06 2006-09-06 Tole d'acier pour la fabrication de structures allegées et procédé de fabrication de cette tole Withdrawn EP1897963A1 (fr)

Priority Applications (20)

Application Number Priority Date Filing Date Title
EP06291413A EP1897963A1 (fr) 2006-09-06 2006-09-06 Tole d'acier pour la fabrication de structures allegées et procédé de fabrication de cette tole
JP2009527173A JP5298017B2 (ja) 2006-09-06 2007-08-27 軽構造物を製造するための鋼板および鋼板を製造する方法
UAA200902135A UA95490C2 (ru) 2006-09-06 2007-08-27 Стальной лист для производства легких конструкций, способ изготовления этого листа и его применение
ES07823448.1T ES2659987T3 (es) 2006-09-06 2007-08-27 Chapa de acero para la fabricación de estructuras ligeras y procedimiento de fabricación de esta chapa
EP07823448.1A EP2064360B1 (fr) 2006-09-06 2007-08-27 Tôle d'acier pour la fabrication de structures allegees et procede de fabrication de cette tôle
PL07823448T PL2064360T3 (pl) 2006-09-06 2007-08-27 Blacha stalowa do wytwarzania lekkich konstrukcji i sposób wytwarzania tej blachy
HUE07823448A HUE036845T2 (hu) 2006-09-06 2007-08-27 Acéllemez könnyûszerkezetek gyártásához, továbbá ilyen lemez gyártási eljárása
PCT/FR2007/001401 WO2008029011A2 (fr) 2006-09-06 2007-08-27 Tôle d'acier pour la fabrication de structures allegees et procede de fabrication de cette tôle
MX2009002411A MX2009002411A (es) 2006-09-06 2007-08-27 Chapa de acero para producir estructuras ligeras y metodo para producirla.
TR2018/02707T TR201802707T4 (tr) 2006-09-06 2007-08-27 Hafif yapıların üretiminde kullanılmak üzere çelik levha ve bu levhanın üretim yöntemi.
BRPI0716877A BRPI0716877B1 (pt) 2006-09-06 2007-08-27 chapa de aço, processo de fabricação de uma chapa de aço, processo de fabricação de peças estruturais e utilização de uma chapa de aço
CA2662741A CA2662741C (fr) 2006-09-06 2007-08-27 Tole d'acier pour la fabrication de structures allegees et procede de fabrication de cette tole
CN2007800330419A CN101563476B (zh) 2006-09-06 2007-08-27 制造轻质结构的钢板以及所述钢板的制造方法
KR1020097004737A KR20090043555A (ko) 2006-09-06 2007-08-27 가벼운 구조체를 제조하기 위한 강판 및 그 강판을 제조하는 방법
RU2009108338/02A RU2416671C2 (ru) 2006-09-06 2007-08-27 Стальная плита для производства легких конструкций и способ производства этой плиты
ZA2009/01377A ZA200901377B (en) 2006-09-06 2009-02-26 Steel plate for producing light structures and method for producing said plate
MA31679A MA30698B1 (fr) 2006-09-06 2009-03-03 Tole d'acier pour la fabrication de structures allegees et procede de fabrication de cette tole.
US12/823,820 US9067260B2 (en) 2006-09-06 2010-06-25 Steel plate for producing light structures and method for producing said plate
US14/513,606 US9718125B2 (en) 2006-09-06 2014-10-14 Steel plate for producing light structures and method for producing said plate
US15/598,951 US10702916B2 (en) 2006-09-06 2017-05-18 Steel plate for producing light structures and method for producing said plate

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP06291413A EP1897963A1 (fr) 2006-09-06 2006-09-06 Tole d'acier pour la fabrication de structures allegées et procédé de fabrication de cette tole

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EP1897963A1 true EP1897963A1 (fr) 2008-03-12

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EP06291413A Withdrawn EP1897963A1 (fr) 2006-09-06 2006-09-06 Tole d'acier pour la fabrication de structures allegées et procédé de fabrication de cette tole
EP07823448.1A Active EP2064360B1 (fr) 2006-09-06 2007-08-27 Tôle d'acier pour la fabrication de structures allegees et procede de fabrication de cette tôle

Family Applications After (1)

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EP07823448.1A Active EP2064360B1 (fr) 2006-09-06 2007-08-27 Tôle d'acier pour la fabrication de structures allegees et procede de fabrication de cette tôle

Country Status (16)

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EP (2) EP1897963A1 (ru)
JP (1) JP5298017B2 (ru)
KR (1) KR20090043555A (ru)
CN (1) CN101563476B (ru)
BR (1) BRPI0716877B1 (ru)
CA (1) CA2662741C (ru)
ES (1) ES2659987T3 (ru)
HU (1) HUE036845T2 (ru)
MA (1) MA30698B1 (ru)
MX (1) MX2009002411A (ru)
PL (1) PL2064360T3 (ru)
RU (1) RU2416671C2 (ru)
TR (1) TR201802707T4 (ru)
UA (1) UA95490C2 (ru)
WO (1) WO2008029011A2 (ru)
ZA (1) ZA200901377B (ru)

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2013050397A1 (en) 2011-10-04 2013-04-11 Tata Steel Nederland Technology Bv Steel product with improved e-modulus and method for producing said product
WO2013171231A1 (en) 2012-05-14 2013-11-21 Tata Steel Nederland Technology Bv High strength steel with increased e-modulus and method for producing said steel
EP2703509A1 (en) 2012-08-28 2014-03-05 Tata Steel Nederland Technology B.V. TiC- and TiB2-Particles reinforced high strength and low density steel with improved E-modulus and method for producing said steel
EP2703510A1 (en) 2012-08-28 2014-03-05 Tata Steel Nederland Technology B.V. Particle-reinforced steel with improved E-modulus and method for producing said steel
WO2014040783A1 (en) 2012-09-14 2014-03-20 Tata Steel Nederland Technology Bv TiC-PARTICLE-REINFORCED HIGH STRENGTH AND LOW DENSITY STEEL PRODUCTS WITH IMPROVED E-MODULUS AND METHOD FOR PRODUCING SAID PRODUCT
JP2015534605A (ja) * 2012-09-14 2015-12-03 タタ、スティール、ネダーランド、テクノロジー、ベスローテン、フェンノートシャップＴａｔａ Ｓｔｅｅｌ Ｎｅｄｅｒｌａｎｄ Ｔｅｃｈｎｏｌｏｇｙ Ｂｖ 弾性率が改良された高強度低密度粒子強化鋼およびその製造方法
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JP2015534605A (ja) * 2012-09-14 2015-12-03 タタ、スティール、ネダーランド、テクノロジー、ベスローテン、フェンノートシャップＴａｔａ Ｓｔｅｅｌ Ｎｅｄｅｒｌａｎｄ Ｔｅｃｈｎｏｌｏｇｙ Ｂｖ 弾性率が改良された高強度低密度粒子強化鋼およびその製造方法
WO2014040783A1 (en) 2012-09-14 2014-03-20 Tata Steel Nederland Technology Bv TiC-PARTICLE-REINFORCED HIGH STRENGTH AND LOW DENSITY STEEL PRODUCTS WITH IMPROVED E-MODULUS AND METHOD FOR PRODUCING SAID PRODUCT
EP3441497A4 (en) * 2016-04-05 2019-08-28 Baoshan Iron & Steel Co., Ltd. LIGHT STEEL AND STEEL SHEET HAVING AN IMPROVED ELASTIC MODULE, AND METHOD OF MANUFACTURING THE SAME
US11078554B2 (en) 2016-04-05 2021-08-03 Baoshan Iron & Steel Co., Ltd. Lightweight steel and steel sheet with enhanced elastic modulus, and manufacturing method thereof
WO2018193411A1 (en) 2017-04-21 2018-10-25 Arcelormittal High formability steel sheet for the manufacture of lightweight structural parts and manufacturing process
WO2018193290A1 (en) 2017-04-21 2018-10-25 Arcelormittal High formability steel sheet for the manufacture of lightweight structural parts and manufacturing process
US11427898B2 (en) 2017-04-21 2022-08-30 Arcelormittal High formability steel sheet for the manufacture of lightweight structural parts and manufacturing process
US11725265B2 (en) 2017-04-21 2023-08-15 Arcelormittal High formability steel sheet for the manufacture of lightweight structural parts and manufacturing process
CN110976796A (zh) * 2019-12-24 2020-04-10 江苏集萃安泰创明先进能源材料研究院有限公司 一种降低残余热应力的非晶合金薄带制备方法
CN110976796B (zh) * 2019-12-24 2021-03-16 江苏集萃安泰创明先进能源材料研究院有限公司 一种降低残余热应力的非晶合金薄带制备方法

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JP2010502838A (ja) 2010-01-28
TR201802707T4 (tr) 2018-03-21
MX2009002411A (es) 2009-03-20
CA2662741A1 (fr) 2008-03-13
MA30698B1 (fr) 2009-09-01
RU2009108338A (ru) 2010-09-20
ES2659987T3 (es) 2018-03-20
JP5298017B2 (ja) 2013-09-25
PL2064360T3 (pl) 2018-06-29
BRPI0716877B1 (pt) 2017-05-02
HUE036845T2 (hu) 2018-08-28
UA95490C2 (ru) 2011-08-10
RU2416671C2 (ru) 2011-04-20
EP2064360B1 (fr) 2017-12-27
WO2008029011A2 (fr) 2008-03-13
CA2662741C (fr) 2012-02-07
BRPI0716877A2 (pt) 2013-10-15
KR20090043555A (ko) 2009-05-06
CN101563476A (zh) 2009-10-21
ZA200901377B (en) 2009-12-30
WO2008029011A3 (fr) 2008-05-02
CN101563476B (zh) 2011-11-16

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