EP1568791A1 - Tôle d'acier laminée à froid de haute résistance et méthode pour fabriquer la même chose - Google Patents

Tôle d'acier laminée à froid de haute résistance et méthode pour fabriquer la même chose Download PDF

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EP1568791A1
EP1568791A1 EP05003676A EP05003676A EP1568791A1 EP 1568791 A1 EP1568791 A1 EP 1568791A1 EP 05003676 A EP05003676 A EP 05003676A EP 05003676 A EP05003676 A EP 05003676A EP 1568791 A1 EP1568791 A1 EP 1568791A1
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Prior art keywords
steel sheet
rolled steel
cold rolled
content
high strength
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German (de)
English (en)
Inventor
Yoshihiko JFE Steel Corporation Ono
Fusato JFE Steel Corporation Kitano
Yasunobu JFE Steel Corporation Nagataki
Yasushi JFE Steel Corporation Tanaka
Hisanori JFE Steel Corporation Ando
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JFE Steel Corp
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JFE Steel Corp
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    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • 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
    • 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
    • C21D8/0478—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 surface treatment
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present invention relates to a high strength cold rolled steel sheet used for automobiles, home appliances, and the like, more particularly to a high strength cold rolled steel sheet having the superior deep drawability and the tensile strength TS of 340 to 590 MPa, and to a manufacturing method thereof.
  • the high strength cold rolled steel sheet having the TS of 340 to 400 MPa and the r value of 1.8 or more and the high strength cold rolled steel sheet having the TS of 400 to 590 MPa and the r value of 1.6 or more, preferably 1.7 or more, are desired.
  • a method comprising the steps of: preparing the IF steel in which the contents of C and N are decreased as small as possible and large amounts of Ti and Nb are added; coiling a hot rolled steel sheet of the IF steel at a high temperature of 680 °C or more so as to decrease the amounts of solute C and N as small as possible, accompanied by the coarsening of the carbides and nitrides; and annealing the cold rolled steel sheet produced from the hot rolled steel sheet so as to promote the nucleation and the growth of the recrystallized grains having the texture preferable to the r value.
  • a method to improve the r value has been also disclosed in Japanese Unexamined Patent Application Publication No. 6-108155 and Japanese Patent No. 3291639, in which the texture preferable to the r value is developed by the formation of Ti(C,S) precipitates, using the Ti bearing IF steel in which the amounts of C and N are decreased as small as possible.
  • Japanese Unexamined Patent Application Publication No. 6-108155 is primarily applied to a mild cold rolled steel sheet having the TS of 260 to 300 MPa, and when the method is applied to the IF high strength cold rolled steel sheet containing the large amounts of P and Mn and having the TS of 340 MPa or more, the large amounts of the phosphides such as Fe-Ti-P and Fe-Nb-P are formed in grain boundaries at coiling after hot rolling. As a result, the r value is extremely decreased.
  • Japanese Patent No. 3291639 it has been proposed that the high strength cold rolled steel sheet with the amount of P has the TS of 340 MPa or more and the deep drawability.
  • the cracking at press forming is caused by the non-uniform microstructure resulting from the segregation of P at casting.
  • the above-mentioned methods need the special manufacturing step, resulting in the increase in the manufacturing cost and the decrease in the productivity. That is, by the method disclosed in Japanese Unexamined Patent Application Publication No. 7-188776, the recrystallization annealing of the hot rolled steel sheet is required. In the method disclosed in Japanese Unexamined Patent Application Publication No. 9-279249, a rolling mill which can be used at the high temperature is required in the annealing furnace. In the method disclosed in Japanese Unexamined Patent Application Publication No. 2001-131643, the pickling, the annealing and the skin pass rolling must be performed twice, respectively.
  • the object of the present invention is to provide a high strength cold rolled steel sheet and a method for manufacturing the same without performing any special manufacturing steps, the high strength cold rolled steel sheet having the TS of 340 to 400 MPa and the r value of 1.8 or more or having the TS of 400 to 590 MPa and the r value of 1.6 or more, preferably 1.7 or more.
  • the object can be attained by the high strength cold rolled steel sheet consisting of 0.015 % or less of C, 1.5 % or less of Si, 0.4 to 3 % of Mn, 0.15 % or less of P, 0.02 % or less of S, 0.1 to 1 % of sol.Al, 0.01 % or less of N, 0.2 % or less of Ti, by mass %, and the balance of Fe and inevitable impurities, in which the following equation (1) is satisfied. 1 ⁇ ([Ti]/48)/([C]/12+[N]/14) where [M] represents the content (mass %) of the element M.
  • the high strength cold rolled steel sheet can be manufactured by the method for manufacturing a high strength cold rolled steel sheet comprising the steps of: heating a slab having the chemical composition described above at 1,080 to 1,350 °C; hot rolling the heated slab at a finishing temperature between (the Ar3 transformation temperature-20) °C and (the Ar3 transformation temperature+150) °C into a hot rolled steel sheet; coiling the hot rolled steel sheet at a coiling temperature CT which satisfies the following equation (5); cold rolling the hot rolled steel sheet with a reduction of 50 to 90 % into a cold rolled steel sheet; and continuously annealing the cold rolled steel sheet at a temperature of 750 to 870 °C or box annealing the cold rolled steel sheet at a temperature of 600 to 750 °C.
  • [M] represents the content (mass %) of the element M.
  • the slab containing 0.002 % of C, 0.25 % of Si, 0.08 % of P, 0.007 % of S, 0.015 % of Nb, 0.03 % of Ti, 0.002 % of N, and 0.001 % of B was heated to 1,250 °C, in which the contents of sol.Al and Mn were varied from 0.01 to 1.2 % and from 0.6 to 1.8 %, respectively.
  • the slab was hot rolled to 3 mm thick, followed by soaking at 580 °C for one hour as the coiling simulation.
  • the hot rolled steel sheet was cold rolled to 0.75 mm thick, continuously annealed at 820 °C for 60 seconds, and subjected to skin pass rolling with the elongation of 0.7 %.
  • the r value and the TS were evaluated by the following methods.
  • the r value and the TS were measured using JIS No. 5 test pieces cut in the direction of 0° , 45° , and 90° to the rolling direction, respectively.
  • the average value of the r value and the TS was calculated with the following equation, respectively.
  • the average value ([T 0 ]+2[T 45 ]+[T 90 ])/4, where [T 0 ], [T 45 ] and [T 90 ] are the values of the r value or the TS measured in the direction of 0° , 45° , and 90° to the rolling direction, respectively.
  • Fig. 1 shows the relationship between the content of sol.Al and the r value and the TS.
  • black circles indicate the results obtained when the content of Mn is 1.8 %
  • white circles indicate the results obtained when the total content of sol.Al and Mn is 1.8 %.
  • the r value is 1.6 or more at the sol.Al content of 0.1 % or more, is 1.7 or more at the sol.Al content of 0.2 to 0.7 %, and decreases at the sol.Al content of more than 0.7 %.
  • the TS exceeds 460 MPa at the sol.Al content of 0.1 % or more and increases with the increase in the sol.Al content.
  • the increase in TS is 35 MPa when the content of the sol.Al is increased by 1 %. Since it is approximately equivalent to solid solution hardenability of Mn, when the total content of sol.Al and Mn is set to 1.8 %, the relation between the TS and the r value, in which the TS is substantially constant, can be obtained as shown with the white circles. Therefore, it is understood that when the sol.Al is added and the content of Mn is decreased, the high r value can be obtained with the constant TS.
  • the TS is more than 400 MPa
  • the content of sol.Al is controlled in the range of 0.1 to 1 %, preferably 0.2 to 0.7 %, the high r value of 1.6 or more, preferably 1.7 or more can be obtained, respectively.
  • the reason why the high r value becomes high when the content of sol.Al is set in the range of 0.1 to 1 % is considered as follows. That is, since Al increases the Ar3 transformation temperature, the coarsening of the carbides and the decrease in the amount of solute C are caused by the precipitation of the at the high temperature below the Ar3 transformation temperature through the transformation from the austenite into the ferrite after the hot rolling; hence, the recrystallization texture preferable to the r value is developed at annealing. In addition, it may be also believed that the change in the cold rolling texture caused by the presence of Al contributes to the improvement in the r value.
  • the contents of Si and P are set to 1.5 % or less and 0.15 % or less, respectively.
  • Si and P tend to cause the decrease in the adhesion of the coating, and hence the contents of Si and P are preferably set to 0.5 % or less and 0.08 % or less, respectively.
  • the amounts of Si and P are preferably set to 0.003 % or more and 0.01 % or more, respectively.
  • C is combined with Ti and Nb to form carbides.
  • the content of C is more than 0.015 %, the amount of carbides is increased, and the r value is extremely decreased.
  • the content of C is set to 0.015 % or less, preferably 0.008 % or less, and more preferably less than 0.004 %. Since C has the effect of increasing the strength by the precipitation hardening when C precipitates as TiC and NbC, the content of C is preferably set to 0.004 % or more for the steel sheet having the TS of approximately 440 MPa.
  • the content of C when the content of C is set to 0.004 to 0.008 %, and the atomic ratio of Ti or Nb against C is 1.0 or more, the increase in the TS can be achieved without decreasing the r value.
  • the content of C is less than 0.0005 %, the ferrite grains coarsen at annealing, so that the surface defect which is called "orange peel" tends to occur at press forming. Therefore, the content of C is preferably set to 0.0005 % or more.
  • Mn is the effective element for the solid solution hardening which is essential to the IF high strength cold rolled steel sheet.
  • the content of Mn In order to obtain the TS of 340 MPa or more, the content of Mn must be set to 0.4 % or more.
  • the r value is extremely decreased, and hence the content of Mn is set to 3 % or less, preferably 2 % or less, and more preferably 1.5 % or less.
  • the reason why the r value is decreased by the increment of Mn content is not clarified; however, it is considered that the decrease in the r value is caused by the interaction of Mn with solute C and by the suppression of the development in the recrystallization texture preferable to the r value at annealing, which is brought about by the fine carbides precipitation and the increase in the amount of solute C at hot rolling because of the decrease in the Ar3 transformation temperature by the addition of Mn.
  • S exists as sulfides in steel.
  • the content of S is more than 0.02 %, the ductility is decreased, and hence the content thereof is set to 0.02 % or less, preferably set to 0.01 % or less.
  • the content of S is preferably set to 0.004 % or more.
  • N When the content of N is more than 0.01 %, fine AlN, NbN, and Nb(C,N) are precipitated in the austenite grain boundaries at slab continuous casting and causes the embrittlement of the grain boundaries, and as a result, the cracking tends to occur in the slab surface at the continuous casting or at the subsequent rough rolling.
  • the content of N is set to 0.01 % or less.
  • the content of N is preferably decreased as small as possible; however, it is too difficult to decrease the content of N below approximately 0.001 % by the smelting technique.
  • Ti has the effect of improving the r value by the grain refinement of the hot bands or by the decrease in the solute C and N with the formation of precipitates thereof.
  • the content of Ti should be controlled to satisfy the following equation (1). 1 ⁇ ([Ti]/48)/([C]/12+[N]/14) where [M] represents the content (mass %) of the element M.
  • the content of Ti is more than 0.2 %, the increase in the r value is small, and hence the content of Ti is set to 0.2 % or less.
  • the content of Ti is preferably set to 0.04 % or less.
  • the content of Ti is preferably set to 0.005 % or more.
  • the balance includes Fe and the inevitable impurities.
  • Nb 0.002 % or more of Nb is preferably further added in order to obtain the higher r value.
  • the contents of Nb, Ti, C, and N must be controlled so as to satisfy the following equation (3). 1 ⁇ ([Nb]/93+[Ti]/48)/([C]/12+[N]/14) where [M] represents the content (mass %) of the element M.
  • the content of Nb is more than 0.02 %, fine NbN and Nb(C,N) precipitate in the austenite grain boundaries at slab continuous casting and lead to the embrittlement of the grain boundaries, and as a result, the cracking tends to occur in the slab surface at the casting or at the subsequent rough rolling.
  • the content of Nb is set to 0.02 % or less.
  • the resistance to the secondary work embrittlement is improved.
  • the content of B is more than 0.003 %, the effect of improving the anti-secondary work embrittlement is small, and the decrease in the r value and the increase in the rolling take place.
  • the content of B is set to 0.003 % or less.
  • At least one element selected from the group consisting of 0.03 to 0.5 % of Cu, 0.03 to 0.5 % of Ni, 0.03 to 0.5 % of Cr, 0.05 to 0.3 % of Mo, and 0.005 to 0.5 % of V may be added. Since Cu and Cr deteriorate the surface quality, the contents thereof are each set to 0.5 % or less. The addition of Ni causes the remarkable increase in cost, and hence the content thereof is set to 0.5 % or less.
  • Mo has the less adverse influence on the resistance to the secondary work embrittlement and is effective for increasing the strength
  • the addition of Mo causes the increase in the yield strength which deteriorates the accuracy of the surface shape after press forming.
  • the content of Mo is set to 0.3 % or less.
  • V has also the less adverse influence on the resistance to the secondary work embrittlement and is effective for increasing the TS, the cost is largely increased when the content is more than 0.5 %.
  • the content of V is set to 0.5 % or less.
  • Ni is preferably added with the content equivalent to that of Cu.
  • Sb and Sn prevents the surface nitridation and oxidation of the steel at slab heating, coiling, or annealing in a box annealing furnace (BAF), a continuous annealing line (CAL), a continuous hot-dip galvanizing line (CGL), and hence improves the non-uniform coating and the deterioration of the coating adhesion.
  • BAF box annealing furnace
  • CAL continuous annealing line
  • CGL continuous hot-dip galvanizing line
  • the surface appearance can also be improved by the prevention of the adhesion of zinc oxides in a molten zinc bath.
  • Sb and Sn reduce the surface oxidation and suppress the degradation in the resistance to the fatigue and the degradation in the toughness after press forming.
  • the high strength cold rolled steel sheet of the present invention can be manufactured by a method comprising the steps of: heating a slab having the chemical composition described above at 1,080 to 1,350 °C; hot rolling the heated slab at a finishing temperature between (the Ar3 transformation temperature-20) °C and (the Ar3 transformation temperature+150) °C into a hot rolled steel sheet; coiling the hot rolled steel sheet at a coiling temperature CT which satisfies the following equation (5) when Nb is not added or the following equation (6) when Nb is added; cold rolling the hot rolled steel sheet with a reduction of 50 to 90 % into a cold rolled steel sheet; and continuously annealing the cold rolled steel sheet at a temperature of 750 to 870 °C or box annealing the cold rolled steel sheet at a temperature of 600 to 750 °C.
  • the heating temperature SRT before hot rolling is set to 1,080 °C or more.
  • the SRT is set to 1,350 °C or less.
  • the primary scale not only the primary scale but also the secondary scale at hot rolling should be sufficiently removed.
  • heating by using a bar heater may also be performed.
  • the finishing temperature FDT of hot rolling is set to the temperature between (the Ar3 transformation temperature-20) °C and (the Ar3 transformation temperature+150) °C for the grain refinement of hot bands.
  • the coiling temperature after hot rolling has the significant influence on the r value of the cold rolled steel sheet of the present invention which contains Al, P, and Ti and also contains Nb when it is necessary to be added.
  • the phosphides such as Fe-Ti-P and Fe-Nb-P unfavorable for the r value tend to be precipitated.
  • the r value is significantly improved due to the coarsening of precipitates and the decrease in solute C by soaking at the high coiling temperature.
  • the coiling temperature is higher than the appropriate temperature, the phosphides as above mentioned are formed, and as a result, the r value is extremely decreased.
  • the coiling temperature is preferably in the range between (the maximum value-40) °C and (the maximum value) °C in the equation (5) or (6).
  • the reduction of the cold rolling is set to 50 to 90 %, preferably to 65 to 80 %.
  • the annealing temperature AT is set to 750 to 870 °C when the continuous annealing is performed in CAL or CGL.
  • the annealing temperature AT is less than 750 °C, the ferrite recrystallization does not occur sufficiently, and hence the high r value cannot be obtained. In addition, the elongation becomes extremely small.
  • the annealing temperature AT is more than 870 °C and more than the Ar3 transformation temperature in case of the steel containing high Mn content, the strength is extremely increased, and the elongation and the n value are extremely decreased.
  • the annealing temperature is preferably 820 °C or more.
  • the annealing temperature is set in the range of 600 to 750 °C.
  • the coating containing zinc may be formed on the annealed steel sheet by the electrolytic coating or the hot-dip coating.
  • the coating containing zinc may be, for example, zinc coating, alloy zinc coating, zinc-nickel alloy coating, or the like.
  • the organic film may be also coated.
  • the annealed steel sheets were immersed in the molten zinc bath at the temperature of 460 °C, and heated at the temperature of 500 °C in the in-line alloying furnace.
  • the amount of zinc on one side surface was 45 g/m 2 .
  • the r value and the TS were measured by the methods described above.
  • the surface defects were measured by eye inspection so as to evaluate the surface quality.
  • the r value is 1.8 or more when the TS is 340 to 400 MPa, the r value is 1.6 or more when the TS is 400 to 590 MPa, and the surface quality is also superior.
  • the r value of the examples of the present invention is significantly high. In particular, when the content of Mn is more than 1 %, the effect described above becomes remarkable.
  • steel sheet No. 30 among those mentioned above corresponding to the conventional low carbon high strength cold rolled steel sheet, in which the content of C and the ratio (Nb+Ti)/(C+N) are not appropriately controlled and in which solute C and Mn coexist, even when the content of sol.Al is increased, the high r value cannot be obtained.
  • steel sheets Nos. 31 and 34 in which the content of Nb and the contents of Nb and sol.Al are out of the range of the present invention, respectively, the surface quality is inferior.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
EP05003676A 2004-02-25 2005-02-21 Tôle d'acier laminée à froid de haute résistance et méthode pour fabriquer la même chose Withdrawn EP1568791A1 (fr)

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JP2004049034 2004-02-25

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US (1) US20060037677A1 (fr)
EP (1) EP1568791A1 (fr)
KR (2) KR20060042036A (fr)
CN (1) CN100439544C (fr)
CA (1) CA2496212C (fr)
TW (1) TWI276692B (fr)

Cited By (3)

* Cited by examiner, † Cited by third party
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EP1960562A1 (fr) * 2005-12-09 2008-08-27 Posco Tole d'acier laminee a froid de haute resistance possedant une excellente propriete de formabilite et de revetement, tole d'acier plaquee de metal a base de zinc fabriquee a partir de cette tole et procede de fabrication de celle-ci
US8353992B2 (en) 2006-11-07 2013-01-15 Nippon Steel Corporation High young's modulus steel plate and method of production of same
US8802241B2 (en) 2004-01-08 2014-08-12 Nippon Steel & Sumitomo Metal Corporation Steel sheet having high young's modulus, hot-dip galvanized steel sheet using the same, alloyed hot-dip galvanized steel sheet, steel pipe having high young's modulus, and methods for manufacturing the same

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DE102009053260B4 (de) * 2009-11-05 2011-09-01 Salzgitter Flachstahl Gmbh Verfahren zum Beschichten von Stahlbändern und beschichtetes Stahlband
JP5786318B2 (ja) * 2010-01-22 2015-09-30 Ｊｆｅスチール株式会社 疲労特性と穴拡げ性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法
JP5786316B2 (ja) * 2010-01-22 2015-09-30 Ｊｆｅスチール株式会社 加工性および耐衝撃特性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法
JP6111522B2 (ja) * 2012-03-02 2017-04-12 Ｊｆｅスチール株式会社 高強度溶融亜鉛めっき鋼板及びその製造方法
KR101647224B1 (ko) * 2014-12-23 2016-08-10 주식회사 포스코 표면품질, 도금밀착성 및 성형성이 우수한 고강도 용융아연도금강판 및 그 제조방법
WO2017033901A1 (fr) * 2015-08-24 2017-03-02 新日鐵住金株式会社 Tôle d'acier plaquée de zinc fondu d'alliage et procédé de fabrication correspondant
WO2017033818A1 (fr) * 2015-08-24 2017-03-02 新日鐵住金株式会社 Essieu ferroviaire
CN106119495B (zh) * 2016-08-19 2019-02-01 武汉钢铁有限公司 一种冷轧中高碳结构钢的制造方法
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CA2496212A1 (fr) 2005-08-25
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KR20070089670A (ko) 2007-08-31
CA2496212C (fr) 2010-01-12
CN100439544C (zh) 2008-12-03
TW200532032A (en) 2005-10-01
KR20060042036A (ko) 2006-05-12
CN1661127A (zh) 2005-08-31

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