EP0870848A1 - Acier au niobium et procédé de fabrication de produits plats à partir de celui-ci - Google Patents
Acier au niobium et procédé de fabrication de produits plats à partir de celui-ci Download PDFInfo
- Publication number
- EP0870848A1 EP0870848A1 EP98200844A EP98200844A EP0870848A1 EP 0870848 A1 EP0870848 A1 EP 0870848A1 EP 98200844 A EP98200844 A EP 98200844A EP 98200844 A EP98200844 A EP 98200844A EP 0870848 A1 EP0870848 A1 EP 0870848A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- niobium
- steel
- maximum
- content
- temperature
- 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.)
- Granted
Links
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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
- C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0426—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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/041—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular fabrication or treatment of ingot or slab
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0436—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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0473—Final recrystallisation annealing
Definitions
- Titanium-free steel indicated in EP-A-0421087, is a steel with ultra-low carbon content, i.e. less than 0.007% by weight, wherein the Nb content is very much higher than the content in nitrogen, of the order of 20 times. Nitrogen is therefore in this steel entirely fixed by nitrobutene niobium and, if boron is used, it remains free and not nitrided. Boron is intended to protect the joints from ferritic grains in order to avoid brittleness to the cold deformation. This steel allows the development to obtain a sheet equivalent or close to IF steels (interstitial free) which have coefficients very high drawing depth, but also a very ⁇ r high (strong plane anisotropy).
- EP-0101740 it is proposed to manufacture flat products whose Nb content is less than or equivalent to the N content. Following hot rolling at a final temperature below Ar 3 , rolling when cold and annealed, products are obtained having low mechanical strength properties, sometimes even lower than the usual minimum requirements.
- a niobium steel is manufactured, in which the Nb content must be at least 6 times that of nitrogen.
- the manufacturing process here also includes hot rolling at a final temperature below Ar 3 , cold rolling and annealing, as well as baking after application of varnish.
- the final products obtained have a much higher niobium content, for properties of mechanical resistance that are not much improved.
- EP-B-0400031 finally proposes, by way of comparative example, a titanium-free niobium steel, having a content comprising more than 12 times the N content. Following hot rolling at a temperature final higher than Ar 3 , cold rolling and annealing, a product is obtained which, according to the patent itself, is not suitable for deep drawing, whatever the degrees of reduction used during cold rolling.
- the object of the present invention is to provide a niobium steel having, in terms of properties mechanical on cold-rolled and annealed strips, a favorable compromise between the properties of resistance, such as for example the elastic limit and the breaking load, and the properties of ductility, such as uniform elongation, coefficient total hardening and elongation.
- niobium steel as described at the beginning, characterized in that this steel contains a stoichiometric niobium content less than that of nitrogen and a boron or zirconium content sufficient to fix nitrogen not fixed by niobium.
- This steel has the advantage of being able have a low niobium content, and therefore not to alter the ductility properties of steel, while obtaining a secure fixation and preferably early nitrogen by the simultaneous presence of boron or zirconium and niobium.
- the content in niobium is at most equal to four times the N content, preferably three times the latter.
- the steel contains an Nb content of less than 0.040% by weight, and preferably between 0.005 and 0.030% by weight.
- it contains a boron content between 0.0005 and 0.012% by weight, preferably between 0.0015 and 0.012% by weight, or a zirconium content between 0.020 and 0.080% by weight.
- the carbon content is equal to or greater than 0.010% by weight.
- the amount of Nb can well be relatively small compared to the content carbon which allows obtaining a steel with favorable mechanical properties.
- This process offers the advantage of fixing supplied with nitrogen in the form of boron nitride or of zirconium as well as in the form of carbonitride niobium, and this at a very early stage in the process.
- the simultaneous presence of boron or zirconium and niobium also promotes reduced grain size austenitic during hot rolling.
- the niobium present is advantageously redissolved.
- the final temperature of hot rolling is preferably equal to or less than 900 ° C. It is precisely at this temperature, that is to say between the transformation temperature ⁇ ⁇ ⁇ (AR 3 ) and 900 ° C, that the boron nitrides and the carbon nitrides of Nb precipitate in the process according to the invention, which fixes the nitrogen.
- the maximum temperature mentioned above is not, however, critical and should only be considered as a preferred temperature.
- the reduction rate is of the order of 40 to 85%, preferably 55-80%.
- the niobium steel according to the invention is usually a steel produced by conversion or of electrical production, classic, which is cast in continued.
- This steel must be extra soft, i.e. have an extremely low carbon content, less than 0.100% by weight, reaching up to minimum contents up to 0.020% or more.
- the carbon content will not exceed not less than 0.010% by weight.
- This steel must also be calmed with aluminum with a content of less than 0.080% by weight.
- Nb, B and Zr are calculated mainly as a function of nitrogen present in the steel being processed.
- Nb added is therefore in reality significantly lower stoichiometrically than nitrogen.
- Nitrogen not fixed by niobium is fixed by B or Zr, which allows an addition of Nb lower than what is usually necessary to obtain properties of sufficient mechanical resistance from a niobium steel, titanium free. This minimal addition of Nb makes it possible to maintain good ductility properties. It also offers advantages economical considering the cost not negligible niobium.
- the steel described above is poured into slabs, which are reheated in a conventional oven, for example a traveling beam oven or a pushing oven, for that they reach a higher temperature at heart or equal to 1000 ° C, which is enough to restore solution of the precipitated niobium.
- a conventional oven for example a traveling beam oven or a pushing oven
- the strip is then cooled so controlled and finally wound at a temperature of around from 625 ° C ⁇ 125 ° C.
- the strip After continuous pickling in conventional lines (HC1 or H 2 SO 4 ), the strip is cold re-rolled, with a thickness reduction rate of between 40 and 85%.
- the cold rolled strip is then subjected to recrystallization annealing to give it the mechanical properties required.
- This annealing can take the form of static annealing, for example in a tight or expanded coil, at a temperature of around 620-680 ° C, or in the form of continuous annealing at a temperature of 680-850 ° C.
- Last annealing can be combined or not with a possible recovery by dip coating or other processes.
- a final rolling step is still performed, in the form of a final work hardening, in order to remove the phenomena of "Lüders bands" and ensure good surface roughness as well as flatness of the product.
- Niobium steel with extremely low carbon content without boron.
- Chemical composition (10 -3 %) VS Mn Yes P S Al N 2 B Nb 50 350 8 12 6 40 6.0 0 50
- Niobium steel according to the invention with addition of boron.
- Chemical composition (10 -3 %) VS Mn Yes P S Al N 2 B Nb 55 300 7 14 3 50 5.6 4.5 7
- Niobium steel according to the invention with addition of boron.
- Chemical composition (10 -3 %) VS Mn Yes P S Al N 2 B Nb 45 270 19 12 6 43 6.0 4.0 12
- Niobium steel with extremely low carbon content with the addition of zirconium.
- Chemical composition (10 -3 %) VS Mn Yes P S Al N 2 B Nb Zr 35 200 5 9 4 47 4.9 0 10 30
- Niobium steels according to the invention offer both mechanical resistance properties well above the lower limits usual and good ductility properties, in therefore providing an entirely favorable compromise for subsequent treatments.
- the niobium steels according to the invention have, on cold-rolled and annealed strips, mechanical properties in the band plane which are significantly independent of management compared to in the sense of rolling as well as a rational contraction in width substantially identical to a contraction rational in thickness. They therefore bring together all conditions for undergoing stamping type treatments difficult and others.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Physics & Mathematics (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Catalysts (AREA)
- Heat Treatment Of Steel (AREA)
- Organic Low-Molecular-Weight Compounds And Preparation Thereof (AREA)
- Compositions Of Oxide Ceramics (AREA)
Abstract
Description
- Nb ≤ 0,040 % en poids, et de
- 0,0015 ≤ B ≤ 0,0120 % en poids
ou de - 0,020 ≤ Zr ≤ 0,080 % en poids,
- un dégrossissage pour réaliser une ébauche de 35 mm ± 10 mm d'épaisseur, à une température moyenne de 1050°C, et
- une finition pour réaliser une bande à chaud d'une épaisseur de 1 à 10 mm, en respectant une température minimale de laminage à chaud qui soit supérieure à la température de transformation de la phase γ à la phase α (Ar3).
Composition chimique (en 10-3 %). | ||||||||
C | Mn | Si | P | S | Al | N2 | B | Nb |
35 | 250 | 6 | 11 | 8 | 44 | 4,2 | 3,6 | 0 |
Température finale du laminage à chaud : | 870°C |
Température de bobinage | 620°C |
Décapage HCl | |
Taux de réduction | 66 % |
Recuit de recristallisation en continu à 700°C pendant 40 sec. suivi d'une trempe à l'eau chaude à 50°C/sec. jusqu'à 400°C, application d'un vieillissement à 400°C pendant 120 sec. et refroidissement par tuyères jusqu'à une température de 120°C, décapage formique, rinçage, et séchage, puis application d'un taux d'écrouissage final de 0,8 %.
Limite d'élasticité | Rp 0,2 = | 235 MPa |
Charge de rupture | Rm = | 340 Mpa |
Allongement à la rupture | A% = | 38 % |
Coefficient d'écrouissage | n = | 0,190/0,200 |
Coefficient d'anisotropie | r travers = | 1,35 |
Coefficient d'anisotropie plane | Δr = | 0,350 |
Coefficient d'anisotropie normale | r moy. | 1,1 |
- Rp 0,2 =
- 175 MPa
- Rm =
- 310 Mpa
- A% =
- 40 %
- n =
- 0,230
- r travers =
- 1,25
- Δr =
- 0,050
- r moy.
- 1,01
Composition chimique (en 10-3 %) | ||||||||
C | Mn | Si | P | S | Al | N2 | B | Nb |
50 | 350 | 8 | 12 | 6 | 40 | 6,0 | 0 | 50 |
Température de bobinage : | 600°C |
Taux de réduction : | 50 % |
- Rp 0,2 =
- 350 MPa
- Rm =
- 440 Mpa
- A% =
- 26 %
- n =
- 0,155
- r travers =
- 1,2
- r long =
- 0,7
- Δr =
- -0,250
- r moy.
- 1,1
Composition chimique (en 10-3 %) | ||||||||
C | Mn | Si | P | S | Al | N2 | B | Nb |
55 | 300 | 7 | 14 | 3 | 50 | 5,6 | 4,5 | 7 |
Température de bobinage : | 500°C |
Taux de réduction : | 80 % |
- Rp 0,2 =
- 290 MPa
- Rm =
- 390 Mpa
- A% =
- 36,5 %
- n =
- 0,195
- r travers =
- 1,1
- Δr =
- -0,005
- r moy.
- 1,0
Composition chimique (en 10-3 %) | ||||||||
C | Mn | Si | P | S | Al | N2 | B | Nb |
45 | 270 | 19 | 12 | 6 | 43 | 6,0 | 4,0 | 12 |
Température finale du laminage à chaud : | 875°C |
Température de bobinage : | 640°C |
Taux de réduction : | 55 % |
- Rp 0,2 =
- 300 MPa
- Rm =
- 400 Mpa
- A% =
- 33 %
- n =
- 0,175
- r travers =
- 1,1
- Δr =
- 0,005
- r moy.
- 1,0
Composition chimique (en 10-3 %) | |||||||||
C | Mn | Si | P | S | Al | N2 | B | Nb | Zr |
36 | 216 | 50 | 7 | 6 | 55 | 3,2 | 0 | 0 | 48 |
Température finale du laminage à chaud: | 885°C. |
Température de bobinage : | 650°C. |
Recuit de recristallisation statique (recuit base) à 610°C. | |
Taux d'écrouissage final : | 0,9 %. |
- Rp 0,2 =
- 224 MPa
- Rm =
- 351 Mpa
- A% =
- 37,6 %
- n =
- 0,206
- Δr =
- 0,308
- r moy.
- 0,96
Composition chimique (en 10-3 %) | |||||||||
C | Mn | Si | P | S | Al | N2 | B | Nb | Zr |
35 | 200 | 5 | 9 | 4 | 47 | 4,9 | 0 | 10 | 30 |
Température de bobinage : | 640°C. |
Taux de réduction : | 58,3 %. |
Recuit de recristallisation statique (recuit base) à 700°C. | |
Taux d'écrouissage final : | 0,8 % |
- Rp 0,2 =
- 255 MPa
- Rm =
- 361 Mpa
- A% =
- 36,4 %
- n =
- 0,190
- Δr =
- 0,040
- r moy.
- 1,01
Claims (19)
- Acier au niobium, extra doux, calmé à l'aluminium et exempt de titane, pour produits plats laminés à froid et recuits, présentant une composition chimique en % en poids comprenant :au maximum 0,100 % de C,au maximum 1,000 % de Mn,au maximum 0,100 % de P,au maximum 0,020 % de S,au maximum 0,080 % de Al,au maximum 0,012 % de N,au maximum 0,500 % de Si,
caractérisé en ce que cet acier contient une teneur en niobium stoechiométriquement inférieure à celle de l'azote et une teneur en bore ou en zirconium suffisante pour fixer l'azote non fixé par le niobium. - Acier au niobium suivant la revendication 1, caractérisé en ce que la teneur en niobium est au maximum égale au quadruple de la teneur en N, de préférence au triple de celle-ci.
- Acier au niobium suivant l'une des revendications 1 et 2, caractérisé en ce qu'il contient une teneur en Nb inférieure à 0,040 % en poids, et de préférence comprise entre 0,005 et 0,030 % en poids.
- Acier au niobium suivant l'une quelconque des revendications 1 à 3, caractérisé en ce qu'il contient une teneur en bore comprise entre 0,0005 et 0,012 % en poids, de préférence entre 0,0015 et 0,012 % en poids.
- Acier au niobium suivant l'une quelconque des revendications 1 à 3, caractérisé en ce qu'il contient une teneur en zirconium comprise entre 0,020 et 0,080 % en poids.
- Acier au niobium suivant l'une quelconque des revendications 1 à 5, caractérisé en ce qu'il contient une teneur en C égale ou supérieure à 0,010 % en poids.
- Acier au niobium, suivant l'une quelconque des revendications 1 à 6, caractérisé en ce qu'il présente, sur des bandes relaminées à froid et recuites, une limite d'élasticité dont les valeurs minimales sont supérieures à 220 MPa et une charge de rupture dont les valeurs minimales sont supérieures à 320 MPa.
- Acier au niobium suivant la revendication 7, caractérisé en ce que la limite d'élasticité est supérieure à 250 MPa, de préférence supérieure à 280 MPa, et en ce que la charge de rupture est supérieure à 350 MPa, de préférence supérieure à 380 MPa.
- Acier au niobium, suivant l'une quelconque des revendications 1 à 8, caractérisé en ce qu'il présente, sur des bandes relaminées à froid et recuites, un allongement à la rupture supérieur ou égal à 32 % et un coefficient d'écrouissage supérieur ou égal à 0,17.
- Acier au niobium suivant l'une quelconque des revendications 1 à 9, caractérisé en ce qu'il présente, sur des bandes relaminées à froid et recuites, des propriétés mécaniques dans le plan de la bande qui sont quasi indépendantes de la direction par rapport au sens de laminage ainsi qu'une contraction rationelle en largeur quasi identique à une contraction rationelle en épaisseur.
- Acier au niobium suivant la revendication 10. caractérisé en ce qu'il présente un Δr situé entre -0,200 et +0,200, de préférence entre -0,100 et +0,100 et un r moyen situé entre 0,9 et 1,1.
- Procédé de fabrication de produits plats laminés à froid et recuits, à base d'un acier au niobium ayant une composition chimique suivant l'une quelconque des revendications 1 à 11, comprenantune coulée de cet acier en brames,un réchauffage des brames à une température supérieure ou égale à 1000°C,un laminage à chaud des brames pour former des bandes, avec une température finale de laminage supérieure à Ar3,un bobinage des bandes à une température de bobinage comprise entre 500 et 750°C,un laminage à froid des bandes avec un taux de réduction prédéterminé ,un recuit de recristallisation, etun passage d'écrouissage final.
- Procédé de fabrication suivant la revendication 12, caractérisé en ce que le réchauffage des brames à lieu de préférence à une température de l'ordre de 1250°C.
- Procédé de fabrication suivant l'une des revendications 12 et 13, caractérisé en ce que la température finale de laminage à chaud est égale ou inférieure à 900°C.
- Procédé de fabrication suivant l'une des revendications 12 à 14, caractérisé en ce que le taux de réduction est de l'ordre de 40 à 85 %, de préférence de 55-80 %.
- Procédé de fabrication suivant l'une des revendications 12 à 15, caractérisé en ce que le recuit de recristallisation est effectué sous la forme d'un recuit statique.
- Procédé de fabrication suivant la revendication 16, caractérisé en ce que le recuit statique est effectué sur des bobines serrées ou expansées à une température de 620 à 680°C point froid.
- Procédé de fabrication suivant l'une des revendications 12 à 15, caractérisé en ce que le recuit de recristallisation est effectué sous la forme d'un recuit continu, avec ou sans revêtement.
- Procédé de fabrication suivant la revendication 18, caractérisé en ce que le recuit de recristalisation continu est effectué à une température de 680 à 850°C.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
BE9700270 | 1997-03-27 | ||
BE9700270A BE1011066A3 (fr) | 1997-03-27 | 1997-03-27 | Acier au niobium et procede de fabrication de produits plats a partir de celui-ci. |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0870848A1 true EP0870848A1 (fr) | 1998-10-14 |
EP0870848B1 EP0870848B1 (fr) | 2003-09-10 |
Family
ID=3890428
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP98200844A Revoked EP0870848B1 (fr) | 1997-03-27 | 1998-03-18 | Acier au niobium et procédé de fabrication de produits plats à partir de celui-ci |
Country Status (7)
Country | Link |
---|---|
EP (1) | EP0870848B1 (fr) |
AT (1) | ATE249528T1 (fr) |
BE (1) | BE1011066A3 (fr) |
DE (1) | DE69817900T2 (fr) |
DK (1) | DK0870848T3 (fr) |
ES (1) | ES2207787T3 (fr) |
PT (1) | PT870848E (fr) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2002059384A2 (fr) * | 2001-01-26 | 2002-08-01 | Usinor | Acier isotrope a haute resistance, procede de fabrication de toles et toles obtenues |
FR2845694A1 (fr) * | 2002-10-14 | 2004-04-16 | Usinor | Procede de fabrication de toles d'acier durcissables par cuisson, toles d'acier et pieces ainsi obtenues |
US7365269B2 (en) | 2002-10-09 | 2008-04-29 | Prysmian Cavi E Sistemi Energia S.R.L. | Method of screening the magnetic field generated by an electrical power transmission line and electrical power transmission line so screened |
RU2578280C2 (ru) * | 2011-09-06 | 2016-03-27 | Арселормитталь Инвестигасьон И Дессарролло Сл | Катаная сталь, которая твердеет посредством выделения частиц после горячего формования и/или закалки в инструменте, имеющая очень высокую прочность и пластичность, и способ ее производства |
Citations (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS55122854A (en) * | 1979-03-15 | 1980-09-20 | Sumitomo Metal Ind Ltd | Welded steel tube having superior butted portion toughness |
EP0101740A1 (fr) * | 1982-02-19 | 1984-03-07 | Kawasaki Steel Corporation | Procede de fabrication d'acier lamine a froid presentant d'excellentes caracteristiques de moulage par pressage |
JPS59123721A (ja) * | 1982-12-29 | 1984-07-17 | Kawasaki Steel Corp | 加工性にすぐれた冷延鋼板の製造方法 |
JPS6160860A (ja) * | 1984-09-03 | 1986-03-28 | Nippon Kokan Kk <Nkk> | メツキ密着性の優れた深絞り用亜鉛メツキ鋼板およびその製造方法 |
JPS6164852A (ja) * | 1984-09-03 | 1986-04-03 | Kawasaki Steel Corp | 面内異方性の極めて少ないプレス加工用非時効性冷延鋼板 |
WO1989007158A1 (fr) * | 1988-01-29 | 1989-08-10 | Stahlwerke Peine-Salzgitter Ag | Tole ou feuillard lamines a froid et procede pour leur fabrication |
EP0421087A2 (fr) * | 1989-08-09 | 1991-04-10 | KABUSHIKI KAISHA KOBE SEIKO SHO also known as Kobe Steel Ltd. | Procédé pour la fabrication d'une tôle d'acier |
JPH04276026A (ja) * | 1991-02-28 | 1992-10-01 | Nippon Steel Corp | 塗装焼付硬化性と2次加工性に優れた深絞り用冷延鋼板の製造方法 |
EP0574814A2 (fr) * | 1992-06-08 | 1993-12-22 | Kawasaki Steel Corporation | Tôle d'acier à résistance élevée laminée à froid, ayant une excellente aptitude à l'emboutissage profond et procédé pour sa fabrication |
DE19547181C1 (de) * | 1995-12-16 | 1996-10-10 | Krupp Ag Hoesch Krupp | Verfahren zur Herstellung eines kaltgewalzten, höherfesten Bandstahles mit guter Umformbarkeit bei isotropen Eigenschaften |
Family Cites Families (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
AU721071B2 (en) * | 1996-02-08 | 2000-06-22 | Jfe Steel Corporation | Steel sheet for 2 piece battery can having excellent formability, anti secondary work embrittlement and corrosion resistance |
US5853903A (en) * | 1996-05-07 | 1998-12-29 | Nkk Corporation | Steel sheet for excellent panel appearance and dent resistance after panel-forming |
-
1997
- 1997-03-27 BE BE9700270A patent/BE1011066A3/fr not_active IP Right Cessation
-
1998
- 1998-03-18 EP EP98200844A patent/EP0870848B1/fr not_active Revoked
- 1998-03-18 AT AT98200844T patent/ATE249528T1/de not_active IP Right Cessation
- 1998-03-18 DE DE69817900T patent/DE69817900T2/de not_active Revoked
- 1998-03-18 ES ES98200844T patent/ES2207787T3/es not_active Expired - Lifetime
- 1998-03-18 DK DK98200844T patent/DK0870848T3/da active
- 1998-03-18 PT PT98200844T patent/PT870848E/pt unknown
Patent Citations (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS55122854A (en) * | 1979-03-15 | 1980-09-20 | Sumitomo Metal Ind Ltd | Welded steel tube having superior butted portion toughness |
EP0101740A1 (fr) * | 1982-02-19 | 1984-03-07 | Kawasaki Steel Corporation | Procede de fabrication d'acier lamine a froid presentant d'excellentes caracteristiques de moulage par pressage |
JPS59123721A (ja) * | 1982-12-29 | 1984-07-17 | Kawasaki Steel Corp | 加工性にすぐれた冷延鋼板の製造方法 |
JPS6160860A (ja) * | 1984-09-03 | 1986-03-28 | Nippon Kokan Kk <Nkk> | メツキ密着性の優れた深絞り用亜鉛メツキ鋼板およびその製造方法 |
JPS6164852A (ja) * | 1984-09-03 | 1986-04-03 | Kawasaki Steel Corp | 面内異方性の極めて少ないプレス加工用非時効性冷延鋼板 |
WO1989007158A1 (fr) * | 1988-01-29 | 1989-08-10 | Stahlwerke Peine-Salzgitter Ag | Tole ou feuillard lamines a froid et procede pour leur fabrication |
EP0421087A2 (fr) * | 1989-08-09 | 1991-04-10 | KABUSHIKI KAISHA KOBE SEIKO SHO also known as Kobe Steel Ltd. | Procédé pour la fabrication d'une tôle d'acier |
JPH04276026A (ja) * | 1991-02-28 | 1992-10-01 | Nippon Steel Corp | 塗装焼付硬化性と2次加工性に優れた深絞り用冷延鋼板の製造方法 |
EP0574814A2 (fr) * | 1992-06-08 | 1993-12-22 | Kawasaki Steel Corporation | Tôle d'acier à résistance élevée laminée à froid, ayant une excellente aptitude à l'emboutissage profond et procédé pour sa fabrication |
DE19547181C1 (de) * | 1995-12-16 | 1996-10-10 | Krupp Ag Hoesch Krupp | Verfahren zur Herstellung eines kaltgewalzten, höherfesten Bandstahles mit guter Umformbarkeit bei isotropen Eigenschaften |
Non-Patent Citations (5)
Title |
---|
DATABASE WPI Section Ch Week 8045, Derwent World Patents Index; Class M23, AN 80-79688C, XP002046101 * |
DATABASE WPI Section Ch Week 8434, Derwent World Patents Index; Class M24, AN 84-211090, XP002046097 * |
DATABASE WPI Section Ch Week 8619, Derwent World Patents Index; Class M27, AN 86-121979, XP002046098 * |
DATABASE WPI Section Ch Week 8620, Derwent World Patents Index; Class M27, AN 86-127775, XP002046100 * |
DATABASE WPI Section Ch Week 9246, Derwent World Patents Index; Class M14, AN 92-376689, XP002046099 * |
Cited By (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2002059384A2 (fr) * | 2001-01-26 | 2002-08-01 | Usinor | Acier isotrope a haute resistance, procede de fabrication de toles et toles obtenues |
FR2820150A1 (fr) * | 2001-01-26 | 2002-08-02 | Usinor | Acier isotrope a haute resistance, procede de fabrication de toles et toles obtenues |
WO2002059384A3 (fr) * | 2001-01-26 | 2002-09-19 | Usinor | Acier isotrope a haute resistance, procede de fabrication de toles et toles obtenues |
US7361237B2 (en) | 2001-01-26 | 2008-04-22 | Usinor | High-strength isotropic steel, method for making steel plates and resulting plates |
KR100879084B1 (ko) * | 2001-01-26 | 2009-01-15 | 아르셀러미탈 프랑스 | 고강도 등방성 강, 강판 제조 방법 및 이에 의한 강판 |
US7365269B2 (en) | 2002-10-09 | 2008-04-29 | Prysmian Cavi E Sistemi Energia S.R.L. | Method of screening the magnetic field generated by an electrical power transmission line and electrical power transmission line so screened |
FR2845694A1 (fr) * | 2002-10-14 | 2004-04-16 | Usinor | Procede de fabrication de toles d'acier durcissables par cuisson, toles d'acier et pieces ainsi obtenues |
WO2004035838A1 (fr) * | 2002-10-14 | 2004-04-29 | Usinor | Procede de fabrication de toles d'acier durcissables par cuisson, toles d'acier et pieces ainsi obtenues |
CN100366760C (zh) * | 2002-10-14 | 2008-02-06 | 法国北方钢铁联合公司 | 制备焙烧硬化钢板的方法及由此获得的钢板和钢材 |
US7540928B2 (en) | 2002-10-14 | 2009-06-02 | Usinor | Process for manufacturing bake hardening steel sheet, and steel sheet and parts thus obtained |
RU2578280C2 (ru) * | 2011-09-06 | 2016-03-27 | Арселормитталь Инвестигасьон И Дессарролло Сл | Катаная сталь, которая твердеет посредством выделения частиц после горячего формования и/или закалки в инструменте, имеющая очень высокую прочность и пластичность, и способ ее производства |
Also Published As
Publication number | Publication date |
---|---|
DE69817900D1 (de) | 2003-10-16 |
DK0870848T3 (da) | 2004-01-12 |
ATE249528T1 (de) | 2003-09-15 |
BE1011066A3 (fr) | 1999-04-06 |
EP0870848B1 (fr) | 2003-09-10 |
DE69817900T2 (de) | 2004-07-22 |
ES2207787T3 (es) | 2004-06-01 |
PT870848E (pt) | 2004-01-30 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP1195447B1 (fr) | Tole d'acier laminee a chaud, tole d'acier laminee a froid et tole d'acier galvanisee par immersion a chaud ayant d'excellentes caracteristiques de durcissement au vieillissement par ecrouissage, et procede pour leur production | |
EP1592816A1 (fr) | Procede de fabrication d une bande d acier dual-phase a structure ferrito-martensitique, laminee a froid et bande obtenue | |
EP1427866B1 (fr) | Procede de fabrication de tubes soudes et tube ainsi obtenu | |
FR2833617A1 (fr) | Procede de fabrication de toles laminees a froid a tres haute resistance d'aciers dual phase micro-allies | |
EP0870848B1 (fr) | Acier au niobium et procédé de fabrication de produits plats à partir de celui-ci | |
US6143100A (en) | Bake-hardenable cold rolled steel sheet and method of producing same | |
FR2761081A1 (fr) | Procede de fabrication d'une tole d'acier electrique a grains orientes pour la fabrication notamment de circuits magnetiques de transformateurs | |
EP0922777A1 (fr) | Produit plat, tel que tÔle, d'un acier à haute limite d'élasticité montrant une bonne ductilité et procédé de fabrication de ce produit | |
JP4670135B2 (ja) | 歪時効硬化特性に優れた熱延鋼板の製造方法 | |
JP3925064B2 (ja) | プレス成形性と歪時効硬化特性に優れた溶融亜鉛めっき鋼板およびその製造方法 | |
JPH0144771B2 (fr) | ||
JPH0559970B2 (fr) | ||
EP0703298B1 (fr) | Procédé de fabrication d'un acier présentant une bonne aptitude à la mise en forme et une bonne résistance à l'indentation | |
US4159918A (en) | Method of manufacturing a compound steel material of a high corrosion resistance | |
JP3925063B2 (ja) | プレス成形性と歪時効硬化特性に優れた冷延鋼板およびその製造方法 | |
JP3613139B2 (ja) | 溶融亜鉛めっき鋼板の製造方法 | |
EP1070148B1 (fr) | Procede de fabrication d'une bande d'acier laminee a chaud pour emboutissage | |
BE1011557A4 (fr) | Acier a haute limite d'elasticite montrant une bonne ductilite et procede de fabrication de cet acier. | |
FR2753399A1 (fr) | Tole d'acier lamine a chaud pour emboutissage profond | |
JP3111462B2 (ja) | 高強度焼付硬化性鋼板の製造方法 | |
BE1002517A6 (fr) | Procede de fabrication d'un acier pour emboutissage. | |
WO2012128272A1 (fr) | Procédé permettant d'enrouler une bande en acier maraging laminée à chaud | |
BE1002461A6 (fr) | Procede de fabrication d'une bande d'acier au carbone par laminage a basse temperature. | |
JPH1017937A (ja) | 加工性に優れるフェライト系ステンレス鋼板の製造方法 | |
WO2000003041A1 (fr) | Produit plat, tel que tole, d'un acier a haute limite d'elasticite montrant une bonne ductilite et procede de fabrication de ce produit |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AT BE CH DE DK ES FI FR GB GR IE IT LI LU NL PT SE |
|
AX | Request for extension of the european patent |
Free format text: AL;LT;LV;MK;RO;SI |
|
17P | Request for examination filed |
Effective date: 19990113 |
|
AKX | Designation fees paid |
Free format text: AT BE CH DE DK ES FI FR GB GR IE IT LI LU NL PT SE |
|
17Q | First examination report despatched |
Effective date: 20001018 |
|
GRAH | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOS IGRA |
|
GRAH | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOS IGRA |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AT BE CH DE DK ES FI FR GB GR IE IT LI LU NL PT SE |
|
RBV | Designated contracting states (corrected) |
Designated state(s): AT BE CH DE DK ES FI FR GB GR IE IT LI LU NL PT SE |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D Free format text: NOT ENGLISH |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: NV Representative=s name: DR. LUSUARDI AG |
|
REF | Corresponds to: |
Ref document number: 69817900 Country of ref document: DE Date of ref document: 20031016 Kind code of ref document: P |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D Free format text: FRENCH |
|
GBT | Gb: translation of ep patent filed (gb section 77(6)(a)/1977) |
Effective date: 20031212 |
|
REG | Reference to a national code |
Ref country code: SE Ref legal event code: TRGR |
|
REG | Reference to a national code |
Ref country code: DK Ref legal event code: T3 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20040122 Year of fee payment: 7 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: NL Payment date: 20040127 Year of fee payment: 7 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: LU Payment date: 20040130 Year of fee payment: 7 |
|
REG | Reference to a national code |
Ref country code: GR Ref legal event code: EP Ref document number: 20030405023 Country of ref document: GR |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: BE Payment date: 20040205 Year of fee payment: 7 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: CH Payment date: 20040217 Year of fee payment: 7 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: PT Payment date: 20040218 Year of fee payment: 7 Ref country code: IE Payment date: 20040218 Year of fee payment: 7 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GR Payment date: 20040224 Year of fee payment: 7 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: SE Payment date: 20040302 Year of fee payment: 7 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: AT Payment date: 20040303 Year of fee payment: 7 Ref country code: GB Payment date: 20040303 Year of fee payment: 7 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FI Payment date: 20040304 Year of fee payment: 7 Ref country code: DK Payment date: 20040304 Year of fee payment: 7 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20040305 Year of fee payment: 7 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: ES Payment date: 20040322 Year of fee payment: 7 |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2207787 Country of ref document: ES Kind code of ref document: T3 |
|
PLBQ | Unpublished change to opponent data |
Free format text: ORIGINAL CODE: EPIDOS OPPO |
|
PLBI | Opposition filed |
Free format text: ORIGINAL CODE: 0009260 |
|
PLAX | Notice of opposition and request to file observation + time limit sent |
Free format text: ORIGINAL CODE: EPIDOSNOBS2 |
|
26 | Opposition filed |
Opponent name: THYSSENKRUPP STAHL AG Effective date: 20040609 |
|
NLR1 | Nl: opposition has been filed with the epo |
Opponent name: THYSSENKRUPP STAHL AG |
|
PLAX | Notice of opposition and request to file observation + time limit sent |
Free format text: ORIGINAL CODE: EPIDOSNOBS2 |
|
RDAF | Communication despatched that patent is revoked |
Free format text: ORIGINAL CODE: EPIDOSNREV1 |
|
RDAG | Patent revoked |
Free format text: ORIGINAL CODE: 0009271 |
|
RDAE | Information deleted related to despatch of communication that patent is revoked |
Free format text: ORIGINAL CODE: EPIDOSDREV1 |
|
RDAF | Communication despatched that patent is revoked |
Free format text: ORIGINAL CODE: EPIDOSNREV1 |
|
RDAC | Information related to revocation of patent modified |
Free format text: ORIGINAL CODE: 0009299REVO |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: PATENT REVOKED |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
27W | Patent revoked |
Effective date: 20050212 |
|
GBPR | Gb: patent revoked under art. 102 of the ep convention designating the uk as contracting state |
Free format text: 20050212 |
|
R27W | Patent revoked (corrected) |
Effective date: 20050212 |
|
REG | Reference to a national code |
Ref country code: PT Ref legal event code: MP4A Effective date: 20050629 |
|
NLR2 | Nl: decision of opposition |
Effective date: 20050212 |
|
REG | Reference to a national code |
Ref country code: SE Ref legal event code: ECNC |
|
PLAB | Opposition data, opponent's data or that of the opponent's representative modified |
Free format text: ORIGINAL CODE: 0009299OPPO |