EP1375694B1 - Procédé de la fabrication d'une bande d'acier laminée à chaud - Google Patents

Procédé de la fabrication d'une bande d'acier laminée à chaud Download PDF

Info

Publication number
EP1375694B1
EP1375694B1 EP03396059A EP03396059A EP1375694B1 EP 1375694 B1 EP1375694 B1 EP 1375694B1 EP 03396059 A EP03396059 A EP 03396059A EP 03396059 A EP03396059 A EP 03396059A EP 1375694 B1 EP1375694 B1 EP 1375694B1
Authority
EP
European Patent Office
Prior art keywords
range
steel strip
hot
steel
rolled
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
EP03396059A
Other languages
German (de)
English (en)
Other versions
EP1375694B2 (fr
EP1375694A1 (fr
Inventor
Mikko Petteri Hemmilä
Reijo Arvi Liimatainen
Tommi Petteri Liimatainen
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.)
Rautaruukki Oyj
Original Assignee
Rautaruukki Oyj
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
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=8564185&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP1375694(B1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by Rautaruukki Oyj filed Critical Rautaruukki Oyj
Publication of EP1375694A1 publication Critical patent/EP1375694A1/fr
Application granted granted Critical
Publication of EP1375694B1 publication Critical patent/EP1375694B1/fr
Publication of EP1375694B2 publication Critical patent/EP1375694B2/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a steel strip that is hot-rolled to a final thickness of at least 2 mm but no more than 12 mm, where the microstructure of said steel strip comprises at least 95% martensite and/or bainite and where the steel contains, in percentages by weight: 0.08 % - 0.16 % C, 0.5 % - 1.5 % Cr and/or 0.1 % - 0.5 % Mo, ⁇ 0.015 % S and ⁇ 0.03% P, 0.01%- 0.08% Al, and the rest is Fe and unavoidable impurities.
  • the invention also relates to a method for manufacturing said hot-rolled steel strip.
  • known strong steel strips i.e. steels used in rolling
  • have a high manganese content and often also a fairly high carbon content such as for example the hot-rolled steel strip described in the publication US-6 284 063 that has a thickness no more than 5 mm.
  • the steel described in said publication contains, in percentages by weight, 0.08% - 0.25% carbon, 1.2% - 2.0% manganese, 0.02% - 0.05% aluminum and less than 0.07% silicon, as well as up to 0.015% phosphorus and up to 0.003% sulfur, while the hot strip contains over 95% martensite.
  • First the slab is heated up to a temperature 1000° C - 1300° C, pre-rolled within the temperature range 950° C - 1150° C and finished at a final rolling temperature above Ar3.
  • the hot strip produced in this way is cooled down to a coiling temperature in the range of 20° C below the martensite start temperature M S , so that the content of other phase forms except for the martensite were less than 5%.
  • the cooling down to the coiling temperature is preferably realized so that the cooling time in the range 800° C ⁇ 500° C is less than 10 seconds.
  • a tensile strength that is in the range 800 N/mm 2 - 1400 N/mm 2 .
  • the publication US-4 406 713 depicts a method of making high-strength, high-toughness steel with good workability and weldability, said steel containing 0.005% - 0.3% carbon, 0.3% - 2.5% manganese, up to 1.5% silicon, up to 0.1% niobium, up to 0.15% vanadium, up to 0.3% titanium and up to 0.3% zirconium.
  • austenitizing is effected at the temperature 1000° C - 1300° C, and thereafter there is performed first for instance hot-rolling in the temperature range Ar3 - 930° C, when the recrystallization of austenite has significantly retarded, at an area reduction of at least 30%.
  • Publication GB-2 076 425 discloses a process for producing dual-phase steel in which process the steel strip is hot rolled, the hot rolling is finished at about 900°C, and coiled at a temperature of between about 350°C to about 580°C, and in which the strip is subsequently continuously annealed in the two-phase ferrite austenite field in temperatures between 760°C and 830°C with holding time between 1.5 and 3 minutes followed by cooling with a rate of 3.5 to 6 ° C/s to transform at least the bulk of the austenite to martensite.
  • composition of the steel comprising, by weight, 0.03% to 0.25%carbon, 0.3% to 2.5% manganese, up to 1.5% silicon, up to 0.25% molybdenum and up to 2% chromium the remainder being iron except for incidental impurities and residuals in amounts depending on the steelmaking practice.
  • the hot rolled strip is subsequently cold rolled before the mentioned annealing at temperatures between 760°C and 830°C. This latter annealing is terminated by forced or natural air cooling.
  • the object of the present invention is to achieve such a hot-rolled steel strip and its manufacturing method that the steel would not be critical as for the local coiling temperature fluctuations in the strip, that it would be highly weldable, suitable for thermal cutting and bending and had a high strength and particularly a high impact toughness.
  • Another object of the invention is to realize this kind of hot-rolled steel strip and its manufacturing method that would enable economical production costs.
  • the first defined hot-rolled steel strip also contains 0.6% - 1.1% Mn and 0.1% - 0.3% Si; the tensile strength of the steel strip is 700 Mpa - 1500 Mpa with a tensile elongation having an A5 value that is at least 6%, and the yield strength is 600 Mpa - 1400 Mpa.
  • this kind of steel strip is manufactured by a method comprising the following steps: the hot rolling of the steel strip in the temperature range 860° C - 960° C to said final thickness; the direct quenching of said hot-rolled steel strip at a delay no more than 15 seconds from the last rolling pass to the coiling temperature within the range 20° C - 520° C, so that the cooling rate in the direct quenching is at least 30° C/s. There is not performed any tempering annealing.
  • the inventive idea is based on the fact that by reducing the amount of manganese and carbon, as well as by alloying chromium and/or molybdenum, as well as boron when necessary, there can be maintained a good hardening and the following advantages can be achieved.
  • the steel structure is not critical for the segregation of manganese and carbon during the casting process owing to the low manganese and carbon content.
  • the steel properties are not critical for local fluctuations of the coiling temperature in the strip, which facilitates the steel production and has an advantageous effect in the homogeneity of its mechanical properties, which again has a positive influence both in the flatness of the end product and in the residual stress.
  • the steel sheet is highly suitable for welding and laser cutting, and at the same time it has a good fatigue strength irrespective of said thermal treatments. Further, the steel sheet has excellent bending properties, a good impact toughness as well as a good resistance to softening in tempering.
  • the hot-rolled steel strip according to the invention that is directly hot-rolled to the thickness 2 mm - 12 mm can be manufactured as wear-resistant and with different hardnesses, typically in the hardness range 300 HB - 400 HB, as so-called wear-resistant steel plate in the same production method as the structural steel plates, only by changing the analysis and/or the post-rolling cooling rate of the strip, and/or temperature before the coiling, within the scope of the invention.
  • This kind of wear-resistant steel can also be used in targets where the structures require properties typically demanded of structural steel, such as good workability, weldability and impact toughness, which means that the hot-rolled steel strip according to the invention is feasible also as structural steel.
  • all content percentages are percentages by weight, and the rest of the steel that is otherwise not defined is iron, Fe, and unavoidable impurities.
  • the steel according to the invention has a relatively low carbon content, i.e. at least 0.08% C but no more than 0.16 % C for good impact toughness, bendability and weldability.
  • Phosphorus P contained as an impurity may rise up to 0.03%, and respectively sulfur S may rise up to 0.015%, which means that these contents are restricted in order to achieve good impact toughness and bendability.
  • further properties can be improved by treating the melt with Ca or CaSi.
  • the employed killing agent is aluminum, which in the end product can be at least 0.01% Al but no more than 0.08 % Al.
  • Chromium, at least 0.5% Cr but no more than 1.5% Cr, and/or molybdenum is at least 0.1% Mo but no more than 0.5% Mo, are alloyed in order to increase hardening and tempering resistance. This enables precipitation at higher coiling temperatures, which can be used for decreasing and even preventing the softening of the steel, as well as for alleviating strength fluctuations caused by local temperature differences during the cooling of the coil.
  • the manganese content is at least only 0.6% Mn but no more than only 1.1 % Mn.
  • the steel is not as susceptible to the segregation of manganese and carbon, which improves the homogeneity of the microstructure. In tests that were carried out it was observed that this is the way to achieve good bending properties and even mechanical properties in different directions, as well as a high-quality surface as thermally cut.
  • silicon it serves as a killing agent in the steel of the present invention, and it also works as a solid solution hardener in contents that area at least 0.10% Si and up to 0.30 % Si, which has an advantageous effect on the impact toughness and workability.
  • the steel according to the invention can be thermally cut, for instance by laser, into precisely defined shapes. It has been observed that a remarkably smooth cutting surface is achieved in a laser cut object. On the other hand, it has been found out that the strength difference between the basic material and the soft zone created in the technical cutting process, which zone is located in the immediate vicinity of the hardened zone, is relatively small. These together have an advantageous affect in the fatigue strength. In addition, a low carbon content reduces the peak hardness of the hardened zone, so that the cutting surface is not sensitive to embrittlement and cracking, neither in the working of the object nor in practical use.
  • the copper content must be limited to less than 0.3% Cu in order to ensure an excellent surface quality of the hot-rolled strip. If the copper content surpasses 0.3%, it is recommendable also to alloy nickel, at least 0.25 times the copper content. Even if there is no copper in the alloy, the amount of nickel in is restricted to ⁇ 1.5% Ni.
  • the amount of alloyed boron is typically at least 0.0005% B but no more than 0.005% B in order to reduce grain size and to increase the hardenability.
  • the amount of alloyed titanium is typically at least 0.01% Ti but no more than 0. 1% in order to bind the nitrogen N and to prevent the creation of boron nitrides BN, because boron nitride reduces the efficiency of boron as a booster of hardening and a reducer of grain size.
  • the steel according to the invention can, particularly at the lower limit of the carbon content, be well bent with respect to its strength, i.e. welded for instance in an filler-metal-free high-frequency welding, so-called HF welding, into a tube.
  • HF welding high-frequency welding
  • steel is manufactured at a final rolling temperature that remains within the range 860° C - 960° C, to a final thickness of 2 mm -12 mm.
  • the cooling of the strip is begun no later than 15 seconds after the last rolling pass, and it is cooled rapidly, the cooling rate being at least 30°C/s, down to a low coiling temperature in the range 20° C - 520° C.
  • the obtained result is typically a nearly completely bainitic and/or martensitic microstructure, so that the bainite and/or martensite content is at least 95 % by volume.
  • the martensite In the coiling temperature range 20° C - 100° C, martensite is not tempered, whereas when the coiling temperature is at least 100° C, the martensite is tempered, so that for instance in the range 100° C - 200° C, the martensite is mildly tempered, and in the coiling temperature range of about 200° C - 520° C, the martensite is tempered and the carbon precipitated.
  • the coiling was carried out at a lower temper brittleness range, 200° C - 400° C, or the cooling was carried out through said range, temper brittleness was not observed with the combination of this production method and composition.
  • the obtained tensile strength Rm is about 700 Mpa - 1500 Mpa, and the obtained yield strength Rp0.2, i.e. strength at a elongation of 0.2%, is about 600 MPa - 1,400 Mpa.
  • the tensile elongation A5 is correspondingly about 18% - 6%.
  • the yield ratio Y/T is typically in the range 0.8 - 0.96.
  • the carbon content of the steel can be arranged in the range 0.12% - 0.16% C, and the hot-rolled steel strip can in that case be directly quenched to the coiling temperature, which is in the range 20° C - 400° C.
  • the quenching can be made either to low coiling temperatures in the range 20° C - 100° C, or preferably to a coiling temperature over 100° C, but still under 400° C, in which case the residue stress is reduced or disappeared without, however, affecting the hardness of the wear plate.
  • a relatively low coiling temperature in the range 100° C - 200° C, can be applied for example for thinner strips, or a slightly higher coiling temperature, in the range 200° C - 400° C, for example for thicker strips.
  • the carbon content of the steel is arranged in the range 0.08% - 0.12% C, and the hot-rolled steel strip is directly quenched to the coiling temperature, which is within the range 20° C - 520° C.
  • quenching can be performed to low temperatures, in the range 20° C - 100° C, or - for the same reason as above, advantageously to a coiling temperature of over 100° C, but still under 520° C.
  • a relatively low coiling temperature in the range of 100° C - 200° C, can be applied for thinner strips, and for instance a slightly higher coiling temperature, in the range of 200° C - 520° C, can be applied to thicker strips.
  • a slightly higher coiling temperature in the range of 200° C - 520° C, can be applied to thicker strips.
  • structural steel i.e. with a carbon content in the range 0.08% - 0.12%
  • the coiling temperature fluctuations of the above-described order have, however, a fairly restricted effect on the properties of the steel strip, as they remain good irrespective of the coiling temperature.
  • Example 1 Traditional tempering tests were carried out in a laboratory with composition a1 , see table 1, by heating samples with measures 8 ⁇ 100 ⁇ 250 mm, in a furnace for 20 minutes and at the temperature 900° C. The samples were quenched into water and tempered for 2 h at different temperatures. The results are presented in table 2. From the results it is apparent that the material has a low toughness area in the temperature range 250° C - 350° C. On the other hand, the elongation is clearly increased at temper temperatures over 400° C, in which case also the strength starts to drop.
  • Example 2 In the strip rolling line, there was hot-rolled a 6 mm thick strip with a composition a2 by direct quenching at the coiling temperature T COIL . The results are presented in table 3.
  • Example 3 In the strip rolling line, there was hot-rolled a 3 mm thick strip with the composition a2 by direct quenching to the coiling temperature T COIL . The results are presented in table 3. From the results it is apparent that also when coiling at a clearly higher temperature 450° C, there were still achieved the same mechanical properties as in example 2.
  • Example 4 In the strip rolling line, there was hot-rolled a 4 mm thick strip with the composition a2 by directly quenching into the coiling temperature T COIL . The results are presented in table 3. From the results it is apparent that also when coiling at a clearly lower temperature, i.e. at 100° C, there were still achieved the same mechanical properties as in examples 2 and 3.
  • Example 5 In the strip rolling line, there was hot-rolled a 10 mm thick strip with the composition a3 by direct quenching to the coiling temperature T COIL . The results are presented in table 3. From the results it is apparent that strength and impact toughness are somewhat reduced, but the properties are still excellent, as long as the coiling temperature does not surpass about 500 ° C.
  • Example 6 In the strip rolling line there was hot-rolled, with a higher carbon level, a 4 mm thick strip with the compositions b2 and b3 by direct quenching to the coiling temperature T COIL .
  • the coiling temperatures applied in the tests were 100° C, 200° C and 380° C.
  • the results are presented in table 3. From the results it is apparent that strength and hardness are somewhat lowered as the coiling temperature increases, but the properties are still of the same class, as long as the coiling temperature does not surpass about 400° C.
  • Example 7 In the strip rolling line there was hot-rolled, with a higher carbon level, 4 mm thick strip with a composition b 1 and b 2, by directly quenching to the coiling temperature T COIL .
  • the coiling temperatures applied in the tests were 470° C, 515° C and 530° C.
  • the results are presented in table 3. From the results it is apparent that strength and hardness decrease, whereas the elongation is clearly increased as the coiling temperature rises.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Mechanical Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Coating With Molten Metal (AREA)
  • Sewing Machines And Sewing (AREA)
  • Shaping Of Tube Ends By Bending Or Straightening (AREA)
  • Lining Or Joining Of Plastics Or The Like (AREA)

Claims (6)

  1. Bande d'acier ayant une microstructure comprenant de la martensite et/ou de la bainite, et dans laquelle l'acier contient, en pourcentages en poids : 0,08 % à 0,16 % de C, 0,5 % à 1,5 % de Cr et/ou 0,1 % à 0,5 % de Mo, 0,6 % à 1,1 % de Mn, ≤ 0,015 % de S et ≤ 0,03 % de P, 0,01 % à 0,08 % d'Al, 0,1 % à 0,3 % de Si, 0,0005 % à 0,005 % de B et 0,01 % à 0,1 % de Ti le reste étant composé de Fe et impuretés inévitables, la résistance à la traction de la bande d'acier étant de 700 Mpa à 1500 Mpa avec un allongement de tension dont la valeur A5 est au moins de 6 %,
    dans laquelle la bande d'acier est une bande d'acier laminée à chaud à une épaisseur finale d'au moins 2mm mais n'excédant pas 12 mm ; la microstructure comprend au moins 95 % de martensite et/ou de bainite ; et la limite d'élasticité est de 600 Mpa à 1400 Mpa.
  2. Bande d'acier selon la revendication 1, caractérisée en ce que la bande d'acier laminée à chaud a un taux d'élasticité dans la gamme de 0,8 à 0,96.
  3. Procédé pour fabriquer une bande d'acier ayant une microstructure comprenant au moins 95 % de martensite et/ou de bainite, ledit acier contenant en pourcentages en poids : 0,08 % à 0,16 % de C ; 0,5 % à 1,5 % de Cr et/ou 0,1 % à 0,5 % de Mo ; 0,01 % à 0,08 % d'Al ; 0,6 % à 1,1 % de Mn ; 0,1 % à 0,3 % de Si, 0,0005 % à 0,005 % de B et 0,01 % à 0,1 % de Ti ; et également du Fe et impuretés inhérentes, la bande d'acier étant laminée à chaud dans la gamme de températures de 860°C à 960°C, dans lequel le procédé comprend les étapes suivantes :
    ladite bande d'acier laminée à chaud dans la gamme de température fournit une épaisseur finale d'au moins 2 mm mais inférieure à 12 mm pour ladite bande d'acier ;
    cette bande d'acier laminée à chaud est directement trempée dans un délai n'excédant pas 15 secondes depuis la dernière passe de laminage à une température de bobinage dans la gamme de 20°C à 520°C, de sorte que le taux de refroidissement dans ce traitement direct soit d'au moins 30°C/s.
  4. Procédé selon la revendication 3, caractérisé en ce que la teneur en carbone de l'acier est comprise dans la gamme de 0,12 % à 0,16 % de C, et ladite bande d'acier laminée à chaud est directement trempée à la température de bobinage dans la gamme de 20°C à 400°C, ou la température de bobinage dans la gamme de 20°C à 100°C ou dans la gamme de 100°C à 200°C ou dans la gamme de 200° à 400°C.
  5. Procédé selon la revendication 3, caractérisé en ce que la teneur en carbone est comprise dans la gamme de 0,08 % à 0,12 % de C et ladite bande d'acier laminée à chaud est directement traitée à la température de bobinage dans la gamme de 20°C à 520°C, ou à la température de bobinage dans la gamme de 20°C à 100°C, ou à la température de bobinage dans la gamme de 100°C à 200°C, ou dans la gamme de 200°C à 520°C.
  6. Procédé selon la revendication 3, caractérisé en ce qu'aucun recuit de durcissement ni trempe ultérieure ne sont effectués dans le procédé.
EP03396059A 2002-06-19 2003-06-18 Procédé de la fabrication d'une bande d'acier laminée à chaud Expired - Lifetime EP1375694B2 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FI20021188A FI114484B (fi) 2002-06-19 2002-06-19 Kuumavalssattu nauhateräs ja sen valmistusmenetelmä
FI20021188 2002-06-19

Publications (3)

Publication Number Publication Date
EP1375694A1 EP1375694A1 (fr) 2004-01-02
EP1375694B1 true EP1375694B1 (fr) 2005-04-27
EP1375694B2 EP1375694B2 (fr) 2010-11-17

Family

ID=8564185

Family Applications (1)

Application Number Title Priority Date Filing Date
EP03396059A Expired - Lifetime EP1375694B2 (fr) 2002-06-19 2003-06-18 Procédé de la fabrication d'une bande d'acier laminée à chaud

Country Status (7)

Country Link
EP (1) EP1375694B2 (fr)
AT (1) ATE294256T1 (fr)
DE (1) DE60300561T3 (fr)
ES (1) ES2238669T5 (fr)
FI (1) FI114484B (fr)
PT (1) PT1375694E (fr)
SI (1) SI1375694T1 (fr)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2010130871A1 (fr) * 2009-05-11 2010-11-18 Rautaruukki Oyj Procédé de fabrication d'un produit en bande d'acier laminée à chaud et produit de bande d'acier laminée à chaud
EP2576848A1 (fr) 2010-06-07 2013-04-10 Rautaruukki OYJ Procédé pour la production d'un produit de type acier laminé à chaud et acier laminé à chaud
EP2729590A1 (fr) 2011-07-10 2014-05-14 Tata Steel IJmuiden BV Bande d'acier haute résistance laminée à chaud avec résistance élevée au ramollissement haz et son procédé de production
US11225697B2 (en) 2014-12-19 2022-01-18 Nucor Corporation Hot rolled light-gauge martensitic steel sheet and method for making the same
EP3730647B1 (fr) * 2017-12-22 2023-07-12 POSCO Co., Ltd Tôle d'acier laminée à chaud à haute résistance ayant une excellente aptitude au pliage et une excellente ténacité à basse température et son procédé de fabrication

Families Citing this family (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2872442B1 (fr) * 2004-07-05 2006-09-15 Usinor Sa Assemblages soudes a haute densite d'energie d'aciers de construction metallique presentant une excellente tenacite dans la zone fondue, et methode de fabrication de ces assemblages soudes
CN100487150C (zh) * 2005-03-30 2009-05-13 株式会社神户制钢所 化学转化处理性优异高强度热轧钢板
WO2007114261A1 (fr) * 2006-03-31 2007-10-11 Kabushiki Kaisha Kobe Seiko Sho Feuille d'acier haute resistance laminee a froid d'excellente compatibilite avec un traitement chimique
US7846275B2 (en) 2006-05-24 2010-12-07 Kobe Steel, Ltd. High strength hot rolled steel sheet having excellent stretch flangeability and its production method
FI122143B (fi) * 2009-10-23 2011-09-15 Rautaruukki Oyj Menetelmä korkealujuuksisen sinkityn muotovalmisteen valmistamiseksi sekä muotovalmiste
FI20106275A (fi) * 2010-12-02 2012-06-03 Rautaruukki Oyj Ultraluja rakenneteräs ja menetelmä ultralujan rakenneteräksen valmistamiseksi
CN102134680A (zh) * 2011-04-19 2011-07-27 首钢总公司 一种屈服强度960MPa级超高强钢及其生产方法
CN102345048A (zh) * 2011-06-28 2012-02-08 南阳汉冶特钢有限公司 一种大厚度加硼钢ss400-b钢板及其生产方法
JP6094139B2 (ja) * 2011-12-21 2017-03-15 Ｊｆｅスチール株式会社 強度−伸びバランスに優れた高張力鋼板およびその製造方法
US10837079B2 (en) 2014-01-24 2020-11-17 Rautaruukki Oyj Hot-rolled ultrahigh strength steel strip product
CN104831166B (zh) * 2015-04-17 2016-08-17 河北钢铁股份有限公司邯郸分公司 一种提高焊瓶钢杯口形状均匀性的带钢生产方法
KR101977474B1 (ko) 2017-08-09 2019-05-10 주식회사 포스코 표면 품질, 강도 및 연성이 우수한 도금강판
KR102164078B1 (ko) * 2018-12-18 2020-10-13 주식회사 포스코 성형성이 우수한 고강도 열연강판 및 그 제조방법
KR102237488B1 (ko) 2019-12-16 2021-04-08 주식회사 포스코 펀칭 성형성이 우수한 고경도 강판 및 그 제조방법
CN113574199B (zh) 2019-12-18 2022-11-29 Posco公司 热轧钢板及其制造方法

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2076425B (en) * 1980-05-21 1984-04-04 British Steel Corp Dual-phase steel sheet
DE3440752A1 (de) * 1984-11-08 1986-05-22 Thyssen Stahl AG, 4100 Duisburg Verfahren zur herstellung von warmband mit zweiphasen-gefuege
JPS62180021A (ja) * 1986-02-03 1987-08-07 Nisshin Steel Co Ltd 加工性及び焼付け硬化性に優れた高張力熱延鋼板の製造方法
GB8621903D0 (en) * 1986-09-11 1986-10-15 British Steel Corp Production of steel
JPH06248341A (ja) † 1993-02-23 1994-09-06 Sumitomo Metal Ind Ltd 非調質鋼からの高強度高靱性鋼の製造方法
JP3338499B2 (ja) * 1993-03-16 2002-10-28 日新製鋼株式会社 加工性に優れた高強度熱延鋼板の製造方法
CZ6999A3 (cs) * 1996-07-12 1999-10-13 Thyssen Stahl Ag Ocelový pás válcovaný za tepla a způsob jeho výroby
FR2807068B1 (fr) † 2000-03-29 2002-10-11 Usinor Acier lamine a chaud a tres haute limite d'elasticite et resistance mecanique utilisable notamment pour la realisation de piece de vehicules automobiles

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2010130871A1 (fr) * 2009-05-11 2010-11-18 Rautaruukki Oyj Procédé de fabrication d'un produit en bande d'acier laminée à chaud et produit de bande d'acier laminée à chaud
EP2576848A1 (fr) 2010-06-07 2013-04-10 Rautaruukki OYJ Procédé pour la production d'un produit de type acier laminé à chaud et acier laminé à chaud
EP2729590A1 (fr) 2011-07-10 2014-05-14 Tata Steel IJmuiden BV Bande d'acier haute résistance laminée à chaud avec résistance élevée au ramollissement haz et son procédé de production
US11225697B2 (en) 2014-12-19 2022-01-18 Nucor Corporation Hot rolled light-gauge martensitic steel sheet and method for making the same
EP3730647B1 (fr) * 2017-12-22 2023-07-12 POSCO Co., Ltd Tôle d'acier laminée à chaud à haute résistance ayant une excellente aptitude au pliage et une excellente ténacité à basse température et son procédé de fabrication

Also Published As

Publication number Publication date
ES2238669T3 (es) 2005-09-01
DE60300561T3 (de) 2011-06-09
ES2238669T5 (es) 2011-05-12
ATE294256T1 (de) 2005-05-15
PT1375694E (pt) 2005-07-29
SI1375694T2 (sl) 2005-10-31
DE60300561T2 (de) 2006-02-23
SI1375694T1 (en) 2011-03-31
EP1375694B2 (fr) 2010-11-17
FI114484B (fi) 2004-10-29
FI20021188A0 (fi) 2002-06-19
FI20021188A (fi) 2003-12-20
DE60300561D1 (de) 2005-06-02
EP1375694A1 (fr) 2004-01-02

Similar Documents

Publication Publication Date Title
EP1375694B1 (fr) Procédé de la fabrication d'une bande d'acier laminée à chaud
US5876521A (en) Ultra high strength, secondary hardening steels with superior toughness and weldability
CA2899570C (fr) Tole d'acier epaisse, solide et tres resistante a la traction, et son procede de production
EP2729590B1 (fr) Bande d'acier haute résistance laminée à chaud avec résistance élevée au ramollissement haz et son procédé de production
KR101388334B1 (ko) 내지연 파괴 특성이 우수한 고장력 강재 그리고 그 제조 방법
EP3653736B1 (fr) Bande d'acier laminée à chaud et procédé de fabrication
US20220145414A1 (en) Method for Producing Conventionally Hot-Rolled Profiled Strip Products
JP7411072B2 (ja) 低温衝撃靭性に優れた高強度極厚物鋼材及びその製造方法
JP2004232022A (ja) 伸びおよび伸びフランジ性に優れた二相型高張力鋼板およびその製造方法
JP4207334B2 (ja) 溶接性と耐応力腐食割れ性に優れた高強度鋼板およびその製造方法
US20230058956A1 (en) Hot rolled and steel sheet and a method of manufacturing thereof
JP4379085B2 (ja) 高強度高靭性厚鋼板の製造方法
JP5028785B2 (ja) 高靭性高張力鋼板およびその製造方法
CN108368589B (zh) 具有优异的韧性和耐切割开裂性的高硬度耐磨钢及其制造方法
US20230357876A1 (en) Method of Manufacturing High Strength Steel Tubing from a Steel Composition and Components Thereof
JP3247908B2 (ja) 延性と耐遅れ破壊特性に優れた高強度熱延鋼板およびその製造方法
US20230357877A1 (en) Method for Producing Conventionally Hot-Rolled Strip Products
JP2002363685A (ja) 低降伏比高強度冷延鋼板
WO2012172185A1 (fr) Procédé de fabrication d'un produit en acier à carbone moyen et produit en acier à carbone moyen laminé à chaud
US20220010404A1 (en) Method for Producing Thermo-Mechanically Produced Profiled Hot-Rolled Strip Products
RU2652281C1 (ru) Способ производства горячекатаных листов из высокопрочной стали
JP2023534180A (ja) 熱処理された冷間圧延鋼板及びその製造方法
JP3622246B2 (ja) 強度、靭性及び溶接性に優れた極厚ｈ形鋼の製造方法
JP2007277697A (ja) 耐疲労亀裂伝播特性および脆性亀裂伝播停止特性に優れた高張力厚鋼板およびその製造方法
JP2007119890A (ja) 高靭性高張力鋼板の製造方法

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 BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR

AX Request for extension of the european patent

Extension state: AL LT LV MK

17P Request for examination filed

Effective date: 20040318

17Q First examination report despatched

Effective date: 20040422

AKX Designation fees paid

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050427

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050427

Ref country code: CH

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050427

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050427

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REF Corresponds to:

Ref document number: 60300561

Country of ref document: DE

Date of ref document: 20050602

Kind code of ref document: P

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050618

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20050620

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20050630

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050727

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050727

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050727

REG Reference to a national code

Ref country code: PT

Ref legal event code: SC4A

Effective date: 20050608

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2238669

Country of ref document: ES

Kind code of ref document: T3

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PLBI Opposition filed

Free format text: ORIGINAL CODE: 0009260

PLBI Opposition filed

Free format text: ORIGINAL CODE: 0009260

26 Opposition filed

Opponent name: SSAB TUNNPLAT AB

Effective date: 20051229

REG Reference to a national code

Ref country code: RO

Ref legal event code: EPE

PLAX Notice of opposition and request to file observation + time limit sent

Free format text: ORIGINAL CODE: EPIDOSNOBS2

26 Opposition filed

Opponent name: SSAB TUNNPLAT AB

Effective date: 20051229

Opponent name: THYSSEN KRUPP STAHL AG

Effective date: 20060127

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

ET Fr: translation filed
NLR1 Nl: opposition has been filed with the epo

Opponent name: SSAB TUNNPLAT AB

PLAB Opposition data, opponent's data or that of the opponent's representative modified

Free format text: ORIGINAL CODE: 0009299OPPO

NLR1 Nl: opposition has been filed with the epo

Opponent name: SSAB TUNNPLAT AB

Opponent name: THYSSEN KRUPP STAHL AG

R26 Opposition filed (corrected)

Opponent name: THYSSENKRUPP STEEL AG

Effective date: 20060127

Opponent name: SSAB TUNNPLAT AB

Effective date: 20051229

PLBB Reply of patent proprietor to notice(s) of opposition received

Free format text: ORIGINAL CODE: EPIDOSNOBS3

NLR1 Nl: opposition has been filed with the epo

Opponent name: SSAB TUNNPLAT AB

Opponent name: THYSSENKRUPP STEEL AG

PLAY Examination report in opposition despatched + time limit

Free format text: ORIGINAL CODE: EPIDOSNORE2

PLBC Reply to examination report in opposition received

Free format text: ORIGINAL CODE: EPIDOSNORE3

APAH Appeal reference modified

Free format text: ORIGINAL CODE: EPIDOSCREFNO

APBP Date of receipt of notice of appeal recorded

Free format text: ORIGINAL CODE: EPIDOSNNOA2O

APBQ Date of receipt of statement of grounds of appeal recorded

Free format text: ORIGINAL CODE: EPIDOSNNOA3O

PLAB Opposition data, opponent's data or that of the opponent's representative modified

Free format text: ORIGINAL CODE: 0009299OPPO

APAH Appeal reference modified

Free format text: ORIGINAL CODE: EPIDOSCREFNO

PLAB Opposition data, opponent's data or that of the opponent's representative modified

Free format text: ORIGINAL CODE: 0009299OPPO

PLBP Opposition withdrawn

Free format text: ORIGINAL CODE: 0009264

APBU Appeal procedure closed

Free format text: ORIGINAL CODE: EPIDOSNNOA9O

PUAH Patent maintained in amended form

Free format text: ORIGINAL CODE: 0009272

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: PATENT MAINTAINED AS AMENDED

27A Patent maintained in amended form

Effective date: 20101117

AK Designated contracting states

Kind code of ref document: B2

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR

REG Reference to a national code

Ref country code: NL

Ref legal event code: T3

REG Reference to a national code

Ref country code: SE

Ref legal event code: RPEO

REG Reference to a national code

Ref country code: SK

Ref legal event code: T5

Ref document number: E 116

Country of ref document: SK

REG Reference to a national code

Ref country code: ES

Ref legal event code: DC2A

Ref document number: 2238669

Country of ref document: ES

Kind code of ref document: T5

Effective date: 20110429

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 14

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 15

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 16

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: PT

Payment date: 20180530

Year of fee payment: 16

Ref country code: CZ

Payment date: 20180607

Year of fee payment: 16

Ref country code: LU

Payment date: 20180625

Year of fee payment: 16

Ref country code: SK

Payment date: 20180607

Year of fee payment: 16

Ref country code: NL

Payment date: 20180615

Year of fee payment: 16

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: CH

Payment date: 20180913

Year of fee payment: 10

Ref country code: TR

Payment date: 20180531

Year of fee payment: 16

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: HU

Payment date: 20180605

Year of fee payment: 16

Ref country code: SE

Payment date: 20180620

Year of fee payment: 16

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20180614

Year of fee payment: 16

Ref country code: ES

Payment date: 20180920

Year of fee payment: 16

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20190627

Year of fee payment: 17

REG Reference to a national code

Ref country code: SE

Ref legal event code: EUG

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190619

Ref country code: PT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20191218

Ref country code: CZ

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190618

Ref country code: RO

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190618

REG Reference to a national code

Ref country code: NL

Ref legal event code: MM

Effective date: 20190701

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20190618

REG Reference to a national code

Ref country code: SK

Ref legal event code: MM4A

Ref document number: E 116

Country of ref document: SK

Effective date: 20190618

REG Reference to a national code

Ref country code: SI

Ref legal event code: KO00

Effective date: 20200206

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190701

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190618

Ref country code: HU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190619

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SK

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190618

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190618

Ref country code: SI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190619

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 20201028

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: ES

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190619

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200630

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190618

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: IT

Payment date: 20220610

Year of fee payment: 20

Ref country code: DE

Payment date: 20220613

Year of fee payment: 20

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: BE

Payment date: 20220613

Year of fee payment: 20

Ref country code: AT

Payment date: 20220615

Year of fee payment: 20

REG Reference to a national code

Ref country code: DE

Ref legal event code: R071

Ref document number: 60300561

Country of ref document: DE

REG Reference to a national code

Ref country code: BE

Ref legal event code: MK

Effective date: 20230618

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK07

Ref document number: 294256

Country of ref document: AT

Kind code of ref document: T

Effective date: 20230618