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EP1399598B2 - Procede pour fabriquer des produits en acier de grande resistance et de bonne malleabilite, formes a froid a partir d'un feuillard lamine a chaud - Google Patents

Procede pour fabriquer des produits en acier de grande resistance et de bonne malleabilite, formes a froid a partir d'un feuillard lamine a chaud Download PDF

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Publication number
EP1399598B2
EP1399598B2 EP02738172A EP02738172A EP1399598B2 EP 1399598 B2 EP1399598 B2 EP 1399598B2 EP 02738172 A EP02738172 A EP 02738172A EP 02738172 A EP02738172 A EP 02738172A EP 1399598 B2 EP1399598 B2 EP 1399598B2
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EP
European Patent Office
Prior art keywords
cold
hot
product
temperature
annealing
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
EP02738172A
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German (de)
English (en)
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EP1399598B1 (fr
EP1399598A1 (fr
Inventor
Thomas Heller
Bernhard Engl
Günter STICH
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.)
ThyssenKrupp Steel Europe AG
Original Assignee
ThyssenKrupp Steel Europe AG
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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
    • 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
    • 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
    • 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
    • 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 invention relates to a method for producing a high-strength, from a hot strip cold-worked steel product with good formability.
  • a method of producing high strength hot rolled strip is known from DE 197 10 125 A1 known.
  • the hot strip obtained is cooled at a cooling rate of at least 30 ° C / s and then reeled at a reel temperature of at most 600 ° C. With the hot strip thus obtained, the strength is at least 900 MPa due to the relatively low reel temperature.
  • the hot strip produced by the known method has a good cold workability.
  • This formability can according to the from DE 197 10 125 A1 known processes are further increased by the fact that the hot strip is subjected after coiling a annealing in the temperature range of 500 ° C to 850 ° C.
  • This annealing achieves a material state which offers advantages for components which as a whole still have to have a high strength, above all yield strength, with good formability.
  • By choosing higher annealing temperatures, particularly high strengths can be achieved at extremely low yield strength ratios or equivalent high solidification with good elongation values.
  • the so annealed hot strip is suitable for cold rolling, in which a degree of deformation of at least 30% is achieved.
  • a cold-worked sheet product of high strength, further improved yield ratio and good hardening behavior can be produced.
  • the expansion behavior of the products produced by cold deformation according to the known methods is not sufficient for many applications.
  • the components produced by the known method do not have the necessary deformability after the cold deformation even then. If they are subjected to a recrystallizing annealing after cold working, although the formability increases, the strength is then no longer sufficient.
  • the object of the invention was to provide a method for producing a cold-formed product, which has a high ductility and a correspondingly good formability at elevated strength in the cold-worked state.
  • the invention is based on the surprising finding that activate the strength-enhancing properties of the microalloying elements contained in steels according to the invention in the production of hot strip by annealing the product obtained from the hot strip after reeling by cold working and thereby cold-formed products with particularly high strengths and a can also produce good forming capacity in the cold-formed state, without the need for a procedurally complex compensation would be required.
  • the good formability for example in crash-relevant components, such as bumpers, side impact beams, reinforcing elements, is fully available in order to be able to convert kinetic energy into transformation energy in the event of a collision with other objects on a large scale.
  • the method according to the invention is particularly suitable for the production of components whose dimensional and dimensional stability are just as demanding as their strength in use.
  • a typical example of such an application is for screens which, in picture tubes of televisions or computer monitors, must maintain the shadow mask under uniform tension in a fixed plane due to the heat load during their assembly and operation.
  • the required high strength receives the component thus cold-formed in the course of the heat treatment carried out according to the invention after cold working, so that as a result an exactly shaped, high-strength component with a high yield strength is available.
  • An additional remuneration which can lead to the delay of the component and an impairment of the surface, is then no longer necessary.
  • a prerequisite for the success achieved by the invention is that during the hot processing of the steel used in the invention, the operating parameters including the reel temperature are chosen so that the possible by the presence of a sufficient amount of Mikrolegleitersommen per se possible increase in hardness in the course of reeling is not achieved, but that the micro-alloying elements after reeling in the non-precipitated, dissolved state.
  • the reel temperature according to the invention is always chosen so that it is at a significant distance below the temperature at which the precipitation maximum of the micro-alloying elements would be achieved.
  • the steel alloy used according to the invention comprises steel compositions from which dual phase steels, bainitic steels or complex phase steels can be produced, depending on the particular composition and production conditions.
  • the aim is generally steels with a fine-grained multi-phase structure, in which bainite, ferrite, martensite and retained austenite depending on the type of steel depending on the size are included.
  • this starting material is hot rolled into hot strip.
  • the hot rolling start temperature is chosen so that the micro-alloying elements remain largely dissolved in the steel so that they are available for the effects caused in the last step of the process according to the invention.
  • the initial rolling temperature should be at least 1050 ° C for this purpose.
  • thin-slab or thin strip casting processes are particularly suitable for the production of the primary material, with which it is particularly possible due to the fact that the need for re-heating of the starting material or a solution of the micro-alloying elements does not exist and, on the other hand, the cooling rates of the strand can be high. keep the micro-alloying elements largely dissolved until the start of the hot rolling process.
  • the hot rolling end temperature should preferably be in the austenite region, ie above the Ar 3 temperature, in order to obtain the fine-grained, multiphase microstructure desired according to the invention.
  • composition of the microstructure of the hot strip obtained is determined by the chemical properties, the warm-up, rolling and cooling conditions and the coiler temperatures. It has been found that the effect achieved according to the invention of increasing strength and formability in dual-phase steels is particularly certain when the reel temperature is at most 300 ° C. For steels with a predominantly bainitic structure, this effect is reliably achieved at reel temperatures which are between 350 ° C and 450 ° C. Complex-phase steels should preferably be coiled at temperatures of 450 ° C to 550 ° C.
  • thermoformed state steels of the type used according to the invention have a high strength of at least 550 N / mm 2 .
  • the steels solidify very strongly.
  • the elongation decreases sharply, so that a high-strength, but difficult to deform product is obtained.
  • Due to their reduced formability, such cold formed components have only a small forming reserve and a correspondingly reduced energy absorption capacity. As such, for example, they are only of limited use for the production of components which are to be used as bumpers in crash-prone areas of an automobile.
  • the yield strength of the steel used is further increased.
  • the annealing of its elongation values are raised again approximately to the level at which the ductility of the hot strip was before the cold deformation.
  • the annealing temperatures during annealing following cold working are in the range of 450 ° C to 700 ° C, preferably in the range of 550 ° C to 650 ° C.
  • Glow time and annealing temperature are interchangeable in a limited scope. That is, at high temperatures only low hold times are required and vice versa. Accordingly, the heat treatment can be carried out as a separately performed treatment step in a hood or in a continuous annealing. Annealing, conventionally carried out under conditions which would result in complete recrystallization, would nullify the effect achieved by the invention.
  • This step may, for example, be a galvanizing or other process for coating or passivating the surface of the cold-worked product, which is carried out at temperatures in the range of the temperatures intended for the annealing treatment.
  • the degrees of deformation achieved in the course of cold working amount to 5% to 20%, in particular 5% to 10%.
  • the cold deformation can be carried out, for example, as roll profiling, drawing, pressing or hydroforming. Cold rolling at relatively low degrees of deformation is also suitable.
  • At least one of the elements Ti, Nb and / or V is used as a micro-alloying element in steel according to the invention.
  • these elements can be added in combined amounts that are sufficient to trigger the elimination process effected at the end of the process according to the invention.
  • particularly preferred is the use of Ti, which is characterized by a particularly favorable excretion behavior.
  • Ti is used according to a preferred embodiment of the invention as the sole micro-alloying element, its content should be at least 3.4 times the content of N in order to ensure a sufficient solution potential of the micro-alloying element.
  • the Ti content of the steel is preferably in the range from 0.07 to 0.15% by weight, while the nitrogen content is preferably less than 0.007% by weight. With Ti contents of this order of magnitude, the formation of Feinstauscheidungen with curing effect is optimally supported.
  • the Al content is preferably in the range of 0.015 to 0.08 wt%. or 0.5 to 1.5 wt .-%.
  • Steel sheets produced in accordance with the invention are preferably suitable for cold forming into components whose high demands are placed on high strength coupled with good elongation behavior and correspondingly good deformation behavior and high geometric dimensional stability.
  • components produced by the invention are characterized by low weight and high energy absorption capacity.
  • An example of an advantageous use of steel sheets produced according to the invention is the production of frames for flat screens.
  • components for bodies of motor vehicles or attachments from steel sheets produced according to the invention, which on the one hand have to be particularly strong and, on the other hand, for example in the event of a collision with another vehicle, have to convert the kinetic energies released during the impact into deformation energy.
  • These are u.a. Longitudinal members, so-called “crash boxes", chassis parts, hollow structural parts and reinforcing parts, such as the A, B or C pillar of the car body.
  • Hot rolled strip produced according to the invention is basically suitable for galvanizing. In this case, however, taking place at relatively low temperatures, in particular piecemeal, hot-dip galvanizing, galvanizing, in which temperatures above 750 ° C, are less suitable because it can be exceeded in terms of the effect achieved according to the invention critical temperatures in each processed workpiece ,
  • a composite according to Table 1 steel has been cast on a continuous casting to a pre-slab, which has then been hot-rolled as a starting material with a temperature of 1125 ° C in a hot strip mill to a hot strip.
  • the hot rolling end temperature was 925 ° C.
  • the reel temperature was 475 ° C.
  • the hot strip was pickled and delivered to a cold rolling mill in the pickled state.
  • Table 1 C Si Mn P S al N Cr 0.12 0.46 1.93 0,014 0.001 0.048 0.0061 0.29 Cu Not a word Ni Nb Ti Ti sl V CE 0.056 0,008 0.034 0.001 0,190 0.0081 0,008 0.51
  • G1 sheet metal has not undergone annealing following cold working, while G2 sheet metals are at 500 ° C, G3 sheet metals at 550 ° C, G4 sheet metals at 600 ° C and sheets the Group G5 were annealed at 650 ° C in a hood oven for one hour and then cooled in air.
  • Table 2 shows the material properties determined in the tensile test for each of the sheets of groups G1 - G5.
  • Table 2 group Ser. No. Cold rolling reduction [%] Anlasstemp. [° C] R eL [N / mm 2 ] R p0,2 [N / mm 2 ] R m [N / mm 2 ] R eL / R m [N / mm 2 ] A 80 [%] A gl [%] G1 G1.0 0 - 804 937 0.86 14.4 8.0 G1.1 5 - 845 995 0.85 13.4 6.3 G1.2 10 - 957 1046 0.91 7.4 2.3 G1.3 20 - 1090 1121 0.97 4,9E 1.2 G2 G2.1 5 500 947 967 0.98 12.0 7.0 G2.2 10 500 986 981 1.01 8.7 5.1 G2.3 20 500 1067 1069 1.00 7,1E 0.6 G3 G3.1 5 550 968 986 0.98 13.7 8.7 G3.2 10 550 1026 10
  • Table 3 gives a second example of a steel composition used in the invention.
  • Table 3 C Si Mn P S al N Cr 0.126 0.69 1.79 0,013 ⁇ 0.001 0,050 0.0060 0.33 Cu Not a word Ni Nb Ti B V CE 0,020 0,010 0,040 0.0040 .1470 0.0002 - -
  • a correspondingly alloyed steel was melted and cast into slabs. Subsequently, the slabs were reheated to a temperature of more than 1150 ° C and hot rolled with a hot rolling temperature of at least 850 ° C. After being rewound at a temperature of less than 600 ° C, for a first untreated tape sample T2.0 of the tape, for a 30 minutes at 580 ° C annealed and then air cooled tape sample T2.1, for a at a cold working degree of 10 % only cold rolled strip sample T2.2 and for a cold rolled in accordance with the invention at a cold working degree of 10%, then annealed for 30 minutes at 580 ° C and then cooled in air tape sample T2.3 the mechanical properties R p0,2 , R m , R e / R m A 5 , A 50 and A 80 were determined.
  • these slabs were reheated to a temperature greater than 1150 ° C., with a hot rolling temperature of at least 850 ° C. and a temperature of less than 600 ° C. Then there are six Tape samples T3.0 to T3.2 have been taken.
  • the tape sample T3.2 clearly demonstrates that high-strength cold-formed sheet metal products can be obtained which, as a comparison of the extensibility values shows, are superior in terms of their formability to the undeformed tape sample T3.0.
  • property improvements of the present invention are achieved when cold rolled strip is subjected to much longer times at relatively low temperatures, e.g. 450 ° C to 550 ° C, annealed in a hood.
  • An example of a particularly advantageous use of a steel produced according to the invention is the production of frames in which the shadow masks of television tubes are held.
  • the frame with the shadow mask is exposed for a sufficient time to a temperature typically about 570 ° C.
  • Another advantageous application of the method according to the invention consists in the production of galvanized side impact beams or other crash-relevant components for vehicle bodies.
  • the respective component is first cold-formed, for example, by a deep-drawing operation from inventively produced hot strip.
  • the cold-formed component is then subjected to a piece galvanizing at temperatures in the range of 470 ° C.
  • the component is also maintained at a temperature level at which the invention achieves increasing the ductility and strength sets.
  • the side impact beam thus obtained Due to its good ductility and simultaneously high strength, the side impact beam thus obtained has a particularly high energy absorption capacity, by means of which it converts a large part of the kinetic energy thus released into deformation energy in the event of a collision with another vehicle and requires it for the survival of the occupants Can secure space.

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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)

Claims (17)

  1. Procédé pour la fabrication d'un produit à résistance élevée et de bonne malléabilité, formé à froid à partir d'un feuillard laminé à chaud,
    - dans lequel un acier, qui contient (en % de poids) : C : 0,01 - 0,25 %, Si : 0,01 - 1,50 %, Mn : 0,50 - 2,00 %, P : ≤ 0,08 %, S: ≤ 0,01 %, Al: 0,001 - 1,50 %, Cr: ≤ 0,60 %, Mo: ≤ 0,60 %, N: ≤ 0,02 %,
    ainsi qu'au moins un élément micro-allié, appartenant au groupe Ti: ≤ 0,20 %, NB: ≤ 0,06 %, V: ≤ 0,15 %,
    le complément étant du fer et des impuretés inévitables, est coulé en une matière primaire, telle que des brames, des fines brames ou un feuillard coulé,
    - dans lequel, la matière primaire est laminée à chaud en un feuillard laminé à chaud, en partant d'une température de début de laminage à chaud, à laquelle les éléments de micro-alliage demeurent sensiblement dissouts,
    - dans lequel le feuillard laminé à chaud est bobiné à une température de bobinage inférieure à 600°C,
    - dans lequel le feuillard laminé à chaud est ensuite formé à froid à un degré de formage de 5 % au minimum et de 20 % au maximum, et
    - dans lequel le produit obtenu par formage à froid est recuit à une température de recuit située dans une plage de 450 à 700 °C, sachant que les températures de recuit et les temps de recuit sont inférieurs aux températures et aux temps nécessaires à une recristallisation complète.
  2. Procédé selon la revendication 1, caractérisé en ce que l'acier contient du Ti en tant que seul élément de micro-alliage, et en ce que le rapport entre la teneur en Ti et la teneur en N est d'au moins 3,4.
  3. Procédé selon l'une des revendications précédentes, caractérisé en ce que la température de laminage à chaud est au moins égale à la température Ar3.
  4. Procédé selon l'une des revendications précédentes, caractérisé en ce que la température de bobinage est inférieure à 300 °C.
  5. Procédé selon l'une des revendications 1 à 3, caractérisé en ce que la température de bobinage est de 350 °C à 450 °C.
  6. Procédé selon l'une des revendications 1 à 3, caractérisé en ce que la température de bobinage est de 450 °C à 550 °C.
  7. Procédé selon l'une des revendications précédentes, caractérisé en ce le degré de formage à froid est de 5 % à 10 %.
  8. Procédé selon l'une des revendications précédentes, caractérisé en ce que la température de recuit est égale à 550°C-600°C.
  9. Procédé selon l'une des revendications précédentes, caractérisé en ce que le recuit est exécuté en continu.
  10. Procédé selon l'une des revendications 1 à 8, caractérisé en ce que le recuit est exécuté dans un four à hotte.
  11. Procédé selon l'une des revendications précédentes, caractérisé en ce que le matériau brut est produit sous la forme d'un feuillard coulé dans une installation de laminage de coulée continue.
  12. Procédé selon l'une des revendications précédentes, caractérisé en ce que le produit fabriqué par déformation à froid est un cadre pour des écrans plats.
  13. Procédé selon l'une des revendications 1 à 11, caractérisé en ce que le produit fabriqué par déformation à froid est un composant pour la fabrication de carrosseries de véhicules automobiles ou d'un composant rapporté.
  14. Procédé selon l'une des revendications précédentes, caractérisé en ce qu'on obtient le produit par déformation exécutée à froid sous haute pression interne.
  15. Procédé selon l'une des revendications précédentes, caractérisé en ce qu'on soumet le produit déformé à froid, à une galvanisation.
  16. Procédé selon la revendication 15, caractérisé en ce qu'on exécute la galvanisation sous la forme d'une galvanisation à chaud.
  17. Procédé selon la revendication 15 ou 16, caractérisé en ce que la galvanisation s'effectue à des températures autour de 460°C.
EP02738172A 2001-06-26 2002-06-21 Procede pour fabriquer des produits en acier de grande resistance et de bonne malleabilite, formes a froid a partir d'un feuillard lamine a chaud Expired - Lifetime EP1399598B2 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE10130774 2001-06-26
DE10130774A DE10130774C1 (de) 2001-06-26 2001-06-26 Verfahren zum Herstellen von hochfesten, aus einem Warmband kaltverformten Stahlprodukten mit guter Dehnbarkeit
PCT/EP2002/006870 WO2003002772A1 (fr) 2001-06-26 2002-06-21 Procede pour fabriquer des produits en acier de grande resistance et de bonne malleabilite, formes a froid a partir d'un feuillard lamine a chaud

Publications (3)

Publication Number Publication Date
EP1399598A1 EP1399598A1 (fr) 2004-03-24
EP1399598B1 EP1399598B1 (fr) 2004-10-13
EP1399598B2 true EP1399598B2 (fr) 2011-02-23

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Application Number Title Priority Date Filing Date
EP02738172A Expired - Lifetime EP1399598B2 (fr) 2001-06-26 2002-06-21 Procede pour fabriquer des produits en acier de grande resistance et de bonne malleabilite, formes a froid a partir d'un feuillard lamine a chaud

Country Status (5)

Country Link
EP (1) EP1399598B2 (fr)
AT (1) ATE279540T1 (fr)
DE (2) DE10130774C1 (fr)
ES (1) ES2230500T3 (fr)
WO (1) WO2003002772A1 (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
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US11193188B2 (en) 2009-02-20 2021-12-07 Nucor Corporation Nitriding of niobium steel and product made thereby
EP4403662A1 (fr) 2023-01-18 2024-07-24 voestalpine Stahl GmbH Acier laminé à froid et son procédé de production

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2855184B1 (fr) * 2003-05-19 2006-05-19 Usinor Tole laminee a froid et aluminiee en acier dual phase a tres haute resistance pour ceinture anti-implosion de televiseur, et procede de fabrication de cette tole
US9149868B2 (en) 2005-10-20 2015-10-06 Nucor Corporation Thin cast strip product with microalloy additions, and method for making the same
US9999918B2 (en) 2005-10-20 2018-06-19 Nucor Corporation Thin cast strip product with microalloy additions, and method for making the same
US10071416B2 (en) 2005-10-20 2018-09-11 Nucor Corporation High strength thin cast strip product and method for making the same
DE112006003169B4 (de) * 2005-12-01 2013-03-21 Posco Stahlbleche zum Warmpressformen mit ausgezeichneten Wärmebehandlungs- und Schlageigenschaften, daraus hergestellte Warmpressteile und Verfahren zu deren Herstellung
US20180209011A1 (en) 2015-07-17 2018-07-26 Salzgitter Flachstahl Gmbh Method of producing a hot strip of a bainitic multi-phase steel having a zn-mg-al coating, and a corresponding hot strip
DE102016005532A1 (de) * 2016-05-02 2017-11-02 Vladimir Volchkov Stahl
CN109023105B (zh) * 2018-09-25 2020-11-13 首钢集团有限公司 一种汽车结构用热轧带钢及制造方法
CN110684932B (zh) * 2019-10-12 2021-06-08 唐山钢铁集团有限责任公司 一种1500MPa级冷成形带钢及其生产方法
CN116497266A (zh) * 2022-01-19 2023-07-28 宝山钢铁股份有限公司 一种热轧高强度高塑性钢及其制造方法

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US3950190A (en) † 1974-11-18 1976-04-13 Youngstown Sheet And Tube Company Recovery-annealed cold-reduced plain carbon steels and methods of producing
US4067754A (en) † 1975-02-28 1978-01-10 Armco Steel Corporation Cold rolled, ductile, high strength steel strip and sheet and method therefor
US4082576A (en) † 1976-10-04 1978-04-04 Youngstown Sheet And Tube Company Ultra-high strength low alloy titanium bearing flat rolled steel and process for making
EP0966547B1 (fr) † 1997-03-13 2001-10-04 Thyssen Krupp Stahl AG Procede permettant de fabriquer un feuillard d'acier a resistance et a malleabilite elevees
EP1067203B1 (fr) † 1999-07-07 2004-03-03 Usinor "Procédé de fabrication de bandes en alliage fer-carbone-manganèse, et bandes ainsi produites"

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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Publication number Priority date Publication date Assignee Title
US11193188B2 (en) 2009-02-20 2021-12-07 Nucor Corporation Nitriding of niobium steel and product made thereby
EP4403662A1 (fr) 2023-01-18 2024-07-24 voestalpine Stahl GmbH Acier laminé à froid et son procédé de production
WO2024153701A1 (fr) 2023-01-18 2024-07-25 Voestalpine Stahl Gmbh Acier laminé à froid et son procédé de production

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DE50201321D1 (de) 2004-11-18
EP1399598A1 (fr) 2004-03-24
WO2003002772A1 (fr) 2003-01-09
ES2230500T3 (es) 2005-05-01
DE10130774C1 (de) 2002-12-12
ATE279540T1 (de) 2004-10-15

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