EP2491157A1 - Procédé de production de produit en acier à haute résistance et produit en acier - Google Patents

Procédé de production de produit en acier à haute résistance et produit en acier

Info

Publication number
EP2491157A1
EP2491157A1 EP10824525A EP10824525A EP2491157A1 EP 2491157 A1 EP2491157 A1 EP 2491157A1 EP 10824525 A EP10824525 A EP 10824525A EP 10824525 A EP10824525 A EP 10824525A EP 2491157 A1 EP2491157 A1 EP 2491157A1
Authority
EP
European Patent Office
Prior art keywords
steel
steel product
hot
product
strip
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
EP10824525A
Other languages
German (de)
English (en)
Other versions
EP2491157A4 (fr
Inventor
Tommi Liimatainen
Mikko HEMMILÄ
Petteri Steen
Juha Rajala
Jussi Minkkinen
Sakari Tihinen
Tanja HÄMEENKORPI
Pasi Pekola
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
Application filed by Rautaruukki Oyj filed Critical Rautaruukki Oyj
Publication of EP2491157A1 publication Critical patent/EP2491157A1/fr
Publication of EP2491157A4 publication Critical patent/EP2491157A4/fr
Withdrawn legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

Definitions

  • the invention relates to a hot-dip galvanized steel product. More specifically, the inven- tion relates to the method for producing a hot-dip galvanized steel product according to the preamble of claim 1. In addition, the invention relates to the hot-dip galvanized steel product according to the preamble of claim 12 and the steel product according to the preamble of claim 14 as well as the use according to claim 25. The invention relates especially to producing a high-strength galvanized product, the composition of which product in percentage by weight comprises
  • the invention also relates to a high-strength product, the composition of which is the aforementioned and it may excellently be hot-dip galvanized.
  • steel structures should be protected against corrosion, for which purpose hot-dip galvanizing is widely used as method, because it is an effi- cient and cost-effective way to create a corrosion protective zinc coating on the steel surface.
  • the zinc coating protects the steel even for hundreds of years depending on the environment and the thickness of the layer.
  • Residual stresses in a cold formed steel product can be eliminated by heat treatments after the forming or by surface modifying, but in production at an industrial scale it is not preferred as it calls for an additional work stage.
  • the Japanese patent specification JP8232041 presents a steel composition for forming a thick-walled, high-strength and galvanized structural hollow section, where the carbon content C is 0.04 - 0.12%, ⁇ 0.05% Si, 0.2-2.0% Mn, and 2 or several of the following alloys ⁇ 0.08% Nb, ⁇ 0.08% V and ⁇ 0.05% Ti. According to the specification, ⁇ 0.05% Si improves resistance to the embrittlement phenomenon. Further, according to Euronorm 10025-2, steel with a silicon content of 0.03 - 0.05% reacts poorly to galvanization, because then one moves in the so-called Sandell zone, where the thickness of the zinc layer grows out of control.
  • the yield strength of the galvanized structural hollow section according to the referred specification remains at a level of maximum 460MPa and the high strength classes (over 460MPa) and high impact strength according to this invention are not reached using the teachings of JP8232041. Further, the specification does not teach how to control additive contents in order to achieve better response to galvanization, whereupon it is uncertain, whether hot-dip galvanization of a structural hollow section will succeed. Brief description of the invention
  • the object of this invention is to resolve a product to be hot-dip galvanized to a yield strength of 460 MPa - 600M Pa, and which excellently withstands the stress caused by the liquid metal in hot-dip galvanization.
  • Another object of the invention is to provide a new method for producing a high-strength and galvanized steel product, in which steel there for improving strength are needed no significant amounts of alloys that impede galvanizing and, in addition, increase costs. In addition, there is not necessarily any need for performing stress relief annealing after cold forming or any other finishing stages.
  • characteristic for the method according to the invention is what is mentioned in the characterizing part of claim 1.
  • Characteristic for a product according to the invention to be hot-dip galvanized is what is defined in the characterizing part of claim 12.
  • Characteristic for a steel product according to the invention is furthermore what has been defined in the characterizing part of claim 14.
  • the biggest advantages of the method according to the invention are that it enables hot- dip galvanized high-strength steel with excellent impact strength. In addition, direct quenching speeds up production turnaround, since there is no need to wait for the coil to cool.
  • the biggest advantages with a steel product according to the invention are that it has high strength combined with good impact strength and it may excellently be hot-dip galvanized.
  • the aims of the invention are reached by choosing the composition of the steel of the steel product according to the invention and by direct quenching of the steel slab with the chosen composition in connection with the producing. In other words, the present invention is implemented by combining steel composition and direct quenching according to the invention.
  • Figure 1 shows the main stages of the method according to the invention
  • FIG. 2 is a more detailed presentation of the stages of the method
  • Figure 3 shows a product according to the invention, which is a square hollow structural section
  • Figure 4 shows a product according to the invention, which is a rectangular hollow structural section.
  • FIG 1 there are shown the main stages of the production of a hot-dip steel product according to the present invention.
  • the steel slab is rolled at the rolling stage 5, from which the resulting steel strip is directed to the direct quenching stage 8.
  • the direct quenched steel strip is further directed to cold forming 12, where the steel product is achieved.
  • the produced steel product is directed on to hot-dip galvanizing 14.
  • FIG 2 there is more closely shown the production of a steel product according to the invention.
  • the steel slab is rolled according to stage 4 in figure 2.
  • the rolling 4 is, for instance, performed in such a way that hot rolling at stage 4 is performed at a temperature of 950 - 1280 °C to a thickness of typically 25 - 50 mm, wherefrom it immediately is forwarded to the strip mill at stage 5, where it is rolled to a strip with a final thickness of 2 - 14 mm.
  • the final thickness of the steel strip is minimum 4 mm. It is also advisable that the final thickness of the steel strip is maximum 12.5 mm.
  • the number of passes in the strip mill is typically 5 - 7.
  • the last pass is performed within the temperature range 760 - 960 °C, advisably within the temperature range 850 - 920 °C, especially if the strip is relatively thin, whereupon the rolling forces are lower.
  • direct quenching 8 of the steel strip is started within 15 seconds.
  • the temperature of the steel strip shall be minimum 700 °C.
  • Direct quenching 8 is performed as water quenching in such a way that the quenching speed is 30 - 150 °C/s, advisably the upper limit is maximum 120 °C/s.
  • Direct quenching 8 is performed to a temperature of maximum 300 °C, advisably maximum 100 °C.
  • the steel strip can be coiled at stage 10. Coiling may thus be performed at a temperature range of 30 - 300 °C.
  • Advisably the initial temperature in the coiling 10 is maximum 100 °C, since during coiling of steel at a temperature exceeding 100 °C there may develop a steam mattress, which complicates the process.
  • the microstructure is homogenous and is formed by a main phase, which advisably is low-carbon ferrite and/or low-carbon bainite.
  • the main phase is typically over 90 %.
  • high-carbon bainite and/or residual austenite and/or martensite as very small high-carbon islets.
  • the microstructure does not contain any big grains at all, thanks to which the ductility properties of the steel are especially good taking the strength of the steel into consideration.
  • Preferably direct quenching speed 8 is maximum 120 °C /s, because then one obtains such a microstructure of the steel that gives the steel particularly good mechanical properties, good impact strength included.
  • the final temperature in the direct quenching is maximum 100 °C, because then there is after quenching obtained a flat strip, where also the edges are even and flat.
  • the steel strip is direct quenched 8 directly to coiling temperature and coiled.
  • the treatment of the steel strip is preferably thermo-mechanic, whereupon no post heat treatment after direct quenching 8 is performed, such as tempering, where the steel is heated, after which it is left to cool.
  • tempering where the steel is heated, after which it is left to cool.
  • the mechanical properties of a steel product produced according to the method are good without any need to undertake any cost-adding post heat treatments. Tempering does not significantly improve the mechanical proper- ties of a steel product and it complicates the process.
  • the steel strip is cold formed 12 to the wished product.
  • the product is produced from the steel strip direct quenched 8 in the strip process 5.
  • the coiled steel strip is coiled open and in case of need the steel strip can be slit and/or cut to suitable dimensions.
  • Cold forming 12 is carried out by well-known section and/or hollow section production methods, preferably cold forming 12 is, however, carried out by roll forming from standard cross sections between several twinrolls.
  • the form of the product is deformed at each twinrolls stage.
  • lane joint welding is carried out on the section.
  • the last stage is typically cutting off a continuous product to a wished dimension.
  • the product may be a piece that is cold formed 12 by beveling. As a result of the cold forming 12 there remain residual stresses in the product.
  • the piece of steel is hoisted into a zinc pot, wherein the temperature of the liquid zinc is app. 450°C.
  • the additive contents of the zinc bath according to the invention shall preferably be limited in the case of lead Pb ⁇ 0.02%, tin Sn ⁇ 0.02%, and bismuth Bi, because it has been observed that these increase the tendency to liquid metal embrittlement.
  • the additive contents used in the zinc pot are lead Pb ⁇ 0.02% and tin Sn ⁇ 0.02%.
  • Zinc reacts with steel, forming a coat that offers protection against corrosion. After a sufficient dipping time the high-strength galvanized product is lifted out of the pot and cooled. Cooling can be achieved in well-known ways, for instance in the air.
  • chart 1 it can be seen that in the invention there has been accomplished a product to be galvanized, the yield strength Rp 0,2 of which even exceeds 460 MPa, 460 - 600 Mpa, preferably 500 - 600 MPa, more preferably 550 - 590 MPa and the impact strength of which is minimum 120J/cm 2 also at low, -60 ° C temperatures.
  • the yield strength Rp 0,2 of a steel product according to the invention is thus over 470 MPa, more preferably over 490 MPa, in other words, the yield strength is preferably 470 - 600 MPa, more preferably 490 - 600 MPa and most preferably 500-590 MPa.
  • the achieved high strength has been accomplished by the lowish alloying 2 and direct quenching 8 of the steel product according to the invention.
  • the yield relationship of a product according to the invention (Rp 0,2 / Rm) is over 0.85, preferably over 0.9. A fairly high yield relationship is important from the point of view of the use of the product for instance as a structural hollow section.
  • chart 1 there has also been shown measuring results of steel products after hot-dip galvanizing tests, which were carried out by metal microscope.
  • the corners of galvanized structural hollow sections (steels 1, 2, and 3.1) according to the invention no cracks whatsoever caused by liquid metal embrittlement were discovered.
  • small aberrations in surface quality, generated during the cold forming of the product may occur on the inside surface of the corner.
  • Rl and R2 are reference exam- pies of structural hollow sections of corresponding strength level, the strength of which has been enhanced by alloys without direct quenching 8.
  • the reference tests Rl and R2 caused a visually discernible crack in the inside corner points of the structural hollow section, as they were hot-dip galvanized 14.
  • the steel has a low carbon content C: 0.04 - 0.10% which is advantageous from the point of view of impact strength, beveling and welding properties of the material.
  • the low carbon equivalent of the steel (C + Mn/6 + (Cr + Mo + V)/5 + (Ni + Cu)/15) has also a positive effect on good welding properties.
  • the carbon content C of the steel C is 0.04 - 0.07%, which improves the hot-dip galvanization ability and the aforementioned properties even further.
  • the silicon content of the steel is chosen in the range Si ⁇ 0.03%, the steel is thus a so called low-silicon steel. Then the zinc layer will become thin ( ⁇ 90 ⁇ ) and it has good adhesive properties.
  • Manganese Mn is used 0.3 - 1.2%. 0.3% is needed at least in order to achieve the necessary strength of the steel, on the other hand it has been established that a too high content impairs impact strength in the case of direct quenched steels. In order to secure impact strength, manganese content is preferably 0.4 - 0.9%.
  • Niobium Nb is a potent alloy that increases strength and it has to be alloyed 0.015- 0.10%. Preferably niobium Nb is alloyed maximum 0.08%.
  • Titanium content is limited to Ti ⁇ 0.06%, preferably Ti ⁇ 0.03%, because high Ti contents increase the amount of hard titanium nitrides (TiN), which may have a harmful ef- feet on among other things impact strength, formability properties and elongation.
  • TiN hard titanium nitrides
  • titanium content really is Ti ⁇ 0.02%.
  • N is limited to N: ⁇ 0.01%, preferably N: ⁇ 0.005%.
  • both titanium Ti and nitrogen N is limited to Ti ⁇ 0.06 %, more preferably Ti ⁇ 0.03%, and even more preferably Ti ⁇ 0.02% and N ⁇ 0.005% in order to ensure excellent formability properties.
  • Vanadinium V is added as an alloy that enhances strength, but its content must be limited to V ⁇ 0.05% contents, because it has been established that vanadinium weakens weldability and impact strength.
  • vanadinium content is V ⁇ 0.01%.
  • Phosphorus P content must be limited to P ⁇ 0.02%, in order to keep up good hot-dip galvanization abilities.
  • phosphorus content is limited together with silicon Si, then preferably P(%)+Si(%) ⁇ 0.04%.
  • the content of the steel used for the production of the steel product according to the present invention is:
  • V ⁇ 0.05%, the remaining being iron, unavoidable impurities or residual contents.
  • the composition of the steel used for producing the steel product consists only of the above mentioned alloys, because additional alloys and/or too big contents impair hot-dip galvanization abilities.
  • the aims of the invention are not necessarily reached by too low alloying.
  • direct quenching 8 high strength has been reached in relation to alloying 2, even if the microstructure of the steel mainly is low-carbon ferrite and/or bainite, without containing significant amounts of high-carbon martensite or high-carbon bainite.
  • the main phase is ferrite in such a way that the microstructure advisably is nearly totally ferritic, in addition to which there are small amounts of bainite and/or martensite and/or residual austenite in the form of very small islets with richened carbon content.
  • direct quenching 8 means accelerated cooling immediately after hot rolling.
  • the invention offers a solution for example for producing high-strength galvanized structural hollow sections 16, 18 according to figures 3 and 4, which in connection with hot-dip galvanization 14 are prone to liquid metal embrittlement in the corner points, in which the external radius of curvature R has been marked.
  • Liquid metal embrittlement phenomena occur especially at small external corner radiuses of curvature R, when R ⁇ 5T, where T is the material strength of the product 16, 18.
  • Liquid metal embrittlement may occur also at angle magnitudes >90°, but preferably at angle magnitudes ⁇ 120°.
  • Enhancing of the material strength T may increase the degree of strain hardening of the product 16, 18, which increases liquid metal embrittlement.
  • the degree of strain hardening of the product can be estimated by the formula (B+H)/2T, where a smaller numerical value means a higher degree of strain hardening.
  • enhancing of the material strength complicates rapid quenching of the steel in connection with the direct quenching 8, when one cannot obtain a uni- formly strong material out of too thick a strip, as the interior remains softer than the surface.
  • material thickness of the product 16, 18 according to the invention is 2 - 14mm, preferably, however 4 - 12.5mm.
  • a product 16, 18 according to the invention is meant a cold formed steel product, in which there is cold formed at least one corner.
  • the product comprises at least one corner, the external corner radius of which is ⁇ 5T and preferably, in addition, one or several angles with a magnitude of ⁇ 120°.
  • the steel product 16, 18 according to the invention is an elongated product and most preferably thereby is meant a closed section, such as a structural hollow section.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Coating With Molten Metal (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

L'invention a pour objet un procédé de production d'un produit en acier galvanisé à haute résistance, dont la composition, en pourcentage en poids, comprend : C : 0,04 à 0,10 %, Si : ≤ 0,03 %, Mn : 0,3 à 1,2 %, Nb : 0,015 à 0,10 %, N : ≤ 0,01 %, P : ≤ 0,02 %, S : ≤ 0,02 %, Al : 0,01 à 0,08 %, V : ≤ 0,08 %, le reste étant du fer, des impuretés inévitables ou des teneurs résiduelles. L'invention a également pour objet un produit à haute résistance ayant la composition mentionnée ci-dessus. Conformément à l'invention, il a été établi de façon surprenante que par trempe directe d'acier ayant la composition mentionnée, on obtient un acier à haute résistance ayant d'excellentes propriétés de galvanisation par immersion à chaud.
EP10824525.9A 2009-10-23 2010-10-22 Procédé de production de produit en acier à haute résistance et produit en acier Withdrawn EP2491157A4 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FI20090387A FI122143B (fi) 2009-10-23 2009-10-23 Menetelmä korkealujuuksisen sinkityn muotovalmisteen valmistamiseksi sekä muotovalmiste
PCT/FI2010/050831 WO2011048274A1 (fr) 2009-10-23 2010-10-22 Procédé de production de produit en acier à haute résistance et produit en acier

Publications (2)

Publication Number Publication Date
EP2491157A1 true EP2491157A1 (fr) 2012-08-29
EP2491157A4 EP2491157A4 (fr) 2014-08-20

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EP10824525.9A Withdrawn EP2491157A4 (fr) 2009-10-23 2010-10-22 Procédé de production de produit en acier à haute résistance et produit en acier

Country Status (3)

Country Link
EP (1) EP2491157A4 (fr)
FI (1) FI122143B (fr)
WO (1) WO2011048274A1 (fr)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FI122313B (fi) * 2010-06-07 2011-11-30 Rautaruukki Oyj Menetelmä kuumavalssatun terästuotteen valmistamiseksi sekä kuumavalssattu teräs
FI125290B (fi) * 2011-06-23 2015-08-14 Rautaruukki Oyj Menetelmä teräsputken valmistamiseksi ja teräsputki
US20140205858A1 (en) 2011-09-13 2014-07-24 Tata Steel Ijmuiden B.V. High strength hot dip galvanised steel strip
CN104630623B (zh) * 2015-01-30 2017-03-01 首钢总公司 具有高扩孔性能的热轧酸洗带钢及其生产方法

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EP1041167A1 (fr) * 1998-09-29 2000-10-04 Kawasaki Steel Corporation Feuille mine d'acier haute resistance, feuille d'acier allie haute resistance revetue de zinc et galvanisee a chaud et procede de production correspondant
EP1319725A2 (fr) * 2001-12-13 2003-06-18 ThyssenKrupp Stahl AG Procédé pour la fabrication d'une bande à chaud
EP1375694A1 (fr) * 2002-06-19 2004-01-02 Rautaruukki OYJ Procédé de la fabrication d'une bande d'acier laminée à chaud
US20040040633A1 (en) * 2000-12-16 2004-03-04 Ing Wilfried Hansch Method for the production of hot strip or sheet from a micro-alloyed steel

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FI20090387A0 (fi) 2009-10-23
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EP2491157A4 (fr) 2014-08-20
FI20090387A (fi) 2011-04-24

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