EP1375694B2 - 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

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Publication number
EP1375694B2
EP1375694B2 EP03396059A EP03396059A EP1375694B2 EP 1375694 B2 EP1375694 B2 EP 1375694B2 EP 03396059 A EP03396059 A EP 03396059A EP 03396059 A EP03396059 A EP 03396059A EP 1375694 B2 EP1375694 B2 EP 1375694B2
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Prior art keywords
hot
steel
steel strip
range
rolled
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German (de)
English (en)
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EP1375694A1 (fr
EP1375694B1 (fr
Inventor
Mikko Petteri Hemmilä
Reijo Arvi Liimatainen
Tommi Petteri Liimatainen
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Rautaruukki Oyj
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Rautaruukki Oyj
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • 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 patent publication also discloses a process for producing a hot-rolled steel sheet strip wherein said alloy is subjected to: rolling at a temperature below 950°C, cooling carried out at a rate of more than 20°C per second up to a temperature ranging from 400°C to 600°C.
  • US 6,554,919 utilizes pure bainitic structure teaching that martensite steels indeed have the highest resistance levels, but that it is difficult to produce such structure on a wide-strip train because of the fragility of martensite, which causes the strip to break after rolling, and accordingly, martensite steels make it possible to achieve resistance levels above 1,000 MPa but with very low ductility levels and expansions of less than 8%.
  • US 6,554,919 further describes that an additional heat treatment must be carried out after rolling, because martensite structure is to be obtained by heat treatment after rolling.
  • US 6,554,919 also teach that: "The vanadium increases mechanical resistance and reduces expansion. Vanadium is the necessary element in steel with a bainite structure in order to produce a hardening effect, something that was not expected since the micro-alloying elements have a hardening effect by precipitation but this precipitation ends at a higher temperature and must be carried out in the ferrite domicile in order to be hardening.
  • 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 100° 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 100° 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 would not be 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 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 over 100° C, but still under 520° C.
  • the coiling temperature which is 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.
  • "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. Table 1.
  • Tempering test results with the composition a 1. T temper °C Time h Rp0.2 N/mm 2 Rm N/mm 2 A5 % Charpy-V, J/cm 2 toughness, % (-20° C) (-40° C) (-20° C) (-40° C) *) 972 1072 12.6 20 5 100 2 897 1123 11.7 133 85 40 15 150 2 913 1125 12.0 172 72 65 10 200 2 922 1113 12.4 122 50 40 10 250 2 938 1112 12.2 36 26 10 10 300 2 928 1086 11.7 55 28 10 5 350 2 963 1064 11.8 115 27 40 10 400 2 971 1049 12.6 93 58 20 15 450 2 911 960 14.2 218 85 80 15 500 2 822 901 15.1 251 216 98 80 600 2 741 773 17.3 334 329 100 98 700 2 430 528 21.2 430 451 100 100 *) only quenched
  • 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. Table 3.
  • 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.
  • Table 3 From the results it is apparent that strength and hardness decrease, whereas the elongation is clearly increased as the coiling temperature rises. Table 4.

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  • 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)
  • Lining Or Joining Of Plastics Or The Like (AREA)
  • Sewing Machines And Sewing (AREA)
  • Shaping Of Tube Ends By Bending Or Straightening (AREA)

Claims (5)

  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% - 0,16% de C, 0,5% - 1,5% de Cr et/ou 0,l% - 0,5% de Mo, 0,6% - 1,l% de Mn, ≤ 0,015% de S et ≤ 0,03% de P, 0,01% - 0,08% d'Al, 0,l% - 0,3% de Si, 0,0005% - 0,005% de B et 0,01% - 0,1% de Ti le reste étant composé de Fe et impuretés inévitables, la résistance à la traction de la bande d'acier étant 700 Mpa - 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 2 mm mais n'excédant pas 12 mm; la microstructure comprend au moins 95% de martensite et/ou de bainite; et la limite d'élasticité est 600 Mpa - 1400 Mpa; et la bande d'acier laminée à chaud a un taux d'élasticité dans la gamme 0,8 - 0,96.
  2. 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% - 0,16% de C, 0,5% - 1,5% de Cr et/ou 0,1% - 0,5% de Mo, 0,01% - 0,08% d'Al, 0,6% - 1,1% de Mn, 0,1% - 0,3% de Si, 0,0005% - 0,005% de B et 0,01% - 0, 1 % de Ti, et également du Fe et impuretés inhérentes, la bande d'acier étant laminée à chaud dans la gamme de températures 860°C - 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 100°C - 520°C, de sorte que le taux de refroidissement dans ce traitement direct soit d'au moins 30 °C/s.
  3. Procédé selon la revendication 2, caractérisé en ce que la teneur en carbone de l'acier est comprise dans la gamme 0,12% - 0,16% de C, et ladite bande d'acier laminée à chaud est directement trempée à la température de bobinage dans la gamme 100 °C - 200 °C ou dans la gamme 200 °C - 400 °C.
  4. Procédé selon la revendication 2, caractérisé en ce que la teneur en carbone est comprise dans la gamme 0,08% - 0,12% de C et ladite bande d'acier laminée à chaud est directement traitée à la température de bobinage dans la gamme 100 °C - 200 °C, ou dans la gamme 200 °C - 520 °C.
  5. Procédé selon la revendication 2, 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
FI20021188 2002-06-19
FI20021188A FI114484B (fi) 2002-06-19 2002-06-19 Kuumavalssattu nauhateräs ja sen valmistusmenetelmä

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

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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 (1)

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CN111356781A (zh) * 2017-12-22 2020-06-30 Posco公司 弯曲性和低温韧性优异的高强度热轧钢板及其制造方法

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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
US7960035B2 (en) * 2005-03-30 2011-06-14 Kobe Steel, Ltd. High-strength hot-rolled steel sheet excellent in chemical treatability
KR20080100835A (ko) * 2006-03-31 2008-11-19 가부시키가이샤 고베 세이코쇼 화성 처리성이 우수한 고강도 냉연 강판
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
FI20095528A (fi) * 2009-05-11 2010-11-12 Rautaruukki Oyj Menetelmä kuumavalssatun nauhaterästuotteen valmistamiseksi sekä kuumavalssattu nauhaterästuote
FI122143B (fi) * 2009-10-23 2011-09-15 Rautaruukki Oyj Menetelmä korkealujuuksisen sinkityn muotovalmisteen valmistamiseksi sekä muotovalmiste
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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
EP2729590B1 (fr) 2011-07-10 2015-10-28 Tata Steel IJmuiden BV Bande d'acier haute résistance laminée à chaud avec résistance élevée au ramollissement haz et son procédé de production
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
CN113215501B (zh) 2014-01-24 2022-09-20 罗奇钢铁公司 热轧超高强度钢带产品
KR102596515B1 (ko) 2014-12-19 2023-11-01 누코 코포레이션 열연 경량 마르텐사이트계 강판 및 이의 제조방법
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
WO2021125386A1 (fr) 2019-12-18 2021-06-24 주식회사 포스코 Tôle d'acier laminée à chaud présentant des propriétés de découpage à la presse et une uniformité excellentes, et son procédé de fabrication

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SI1375694T2 (sl) 2005-10-31
ATE294256T1 (de) 2005-05-15
EP1375694A1 (fr) 2004-01-02
PT1375694E (pt) 2005-07-29
DE60300561D1 (de) 2005-06-02
ES2238669T5 (es) 2011-05-12
FI114484B (fi) 2004-10-29
FI20021188A0 (fi) 2002-06-19
EP1375694B1 (fr) 2005-04-27
SI1375694T1 (en) 2011-03-31
DE60300561T2 (de) 2006-02-23
FI20021188A (fi) 2003-12-20
DE60300561T3 (de) 2011-06-09

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