EP3719149A1 - Produit d'acier à dureté élevée et son procédé de fabrication - Google Patents

Produit d'acier à dureté élevée et son procédé de fabrication Download PDF

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Publication number
EP3719149A1
EP3719149A1 EP19185759.8A EP19185759A EP3719149A1 EP 3719149 A1 EP3719149 A1 EP 3719149A1 EP 19185759 A EP19185759 A EP 19185759A EP 3719149 A1 EP3719149 A1 EP 3719149A1
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European Patent Office
Prior art keywords
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steel
steel product
range
temperature
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EP19185759.8A
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German (de)
English (en)
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EP3719149B1 (fr
Inventor
Magnus Larsson
Magnus Gladh
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SSAB Technology AB
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SSAB Technology AB
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Priority to CN202080026935.0A priority Critical patent/CN113785078B/zh
Priority to US17/601,227 priority patent/US20220177996A1/en
Priority to KR1020217035749A priority patent/KR20210149123A/ko
Priority to PCT/EP2020/059424 priority patent/WO2020201438A1/fr
Priority to CN202080026939.9A priority patent/CN113785079B/zh
Priority to PCT/EP2020/059423 priority patent/WO2020201437A1/fr
Priority to JP2021559152A priority patent/JP2022528420A/ja
Priority to BR112021019865A priority patent/BR112021019865A2/pt
Priority to BR112021019860A priority patent/BR112021019860A2/pt
Priority to CA3135144A priority patent/CA3135144A1/fr
Priority to CA3135141A priority patent/CA3135141A1/fr
Priority to US17/601,234 priority patent/US20220177997A1/en
Publication of EP3719149A1 publication Critical patent/EP3719149A1/fr
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    • 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
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • 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
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
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    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • C22C38/105—Ferrous alloys, e.g. steel alloys containing cobalt containing Co and Ni
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/22—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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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 present invention relates to a high-hardness steel strip product exhibiting a good balance of high hardness and excellent mechanical properties such as impact strength and formability/bendability.
  • the present invention further relates to a method of manufacturing the high-hardness steel strip product.
  • High hardness has a direct effect on wear resistance of a steel product, the higher hardness the better wear resistance.
  • high hardness it is meant that the Brinell hardness is at least 450 HBW and especially in the range of 500 HBW to 650 HBW.
  • Wear resistant steels are also known as abrasion resistant steels. They are used in applications in which high resistance against abrasive and shock wear is required. Such applications can be found in e.g . mining and earth moving industry, and waste transportation. Wear resistant steels are used for instance in gravel truck's bodies and excavator buckets, whereby longer service time of the vehicle components is achieved due to the high hardness provided by the wear resistant steels.
  • Wear resistant steels can also function as structural steels for making construction components if the wear resistant steels have sufficient mechanical properties such as formability, weldability and fatigue resistance that comply with national standards.
  • the advantage of using wear resistant steels in the structural part for construction purposes is that less welding is needed and the weight can be lowered.
  • Such high hardness in a steel product is typically obtained by martensitic microstructure produced by quench hardening steel alloy having high content of carbon (0.41-0.50 wt. %) after austenitization in the furnace.
  • steel plates are first hot-rolled, slowly cooled to room temperature from the hot-rolling heat, reheated to austenitization temperature, equalized and finally quench hardened.
  • This process is hereinafter referred to as the reheating and quenching (RHQ) process.
  • RHQ reheating and quenching
  • steels produced in this way are wear resistant steels disclosed in CN102199737 or some commercial wear resistant steels. Due to the relatively high content of carbon, which is required to achieve the desired hardness, the resulting martensite reaction causes significant internal residual stresses to the steel.
  • CN102392186 and CN103820717 relate to RHQ steel plates having relatively low carbon content (0.25-0.30 wt. % in CN102392186 ; 0.22-0.29 wt. % in CN103820717 ) and also relatively low manganese content.
  • a tempering step after quench hardening is required for making such RHQ steel plates, which inevitably increases the processing efforts and costs.
  • EP2695960 relates to an abrasion-resistant steel product exhibiting excellent resistance to stress corrosion cracking, which steel sheet can be made in a process where direct quenching (DQ) may be performed immediately after hot rolling, without the reheating treatment after hot rolling as in the RHQ process.
  • the steel sheet of EP2695960 has a relatively low carbon content (0.20-0.30 wt. %) and a relatively high manganese content (0.40-1.20 wt. %).
  • the base phase or main phase of the microstructure of the steel product of EP2695960 must be made of tempered martensite.
  • the area fraction of untempered martensite is restricted to 10% or less because the resistance to stress corrosion cracking is reduced in the presence of untempered martensite.
  • the steel product of EP2695960 has a surface hardness of 520 HBW or less.
  • the present invention extends the utilization of the cost-effective thermomechanically controlled processing (TMCP) in conjunction with direct quenching (DQ) and possibly also tempering to produce a high-hardness steel strip product exhibiting excellent formability/bendability and impact strength values.
  • TMCP thermomechanically controlled processing
  • DQ direct quenching
  • the object of the present invention is to solve the problem of providing a high-hardness steel strip product exhibiting excellent formability/bendability and impact strength values.
  • the problem is solved by the combination of specific alloy designs with cost-efficient TMCP procedures which produces a metallographic microstructure comprising mainly martensite.
  • the present invention provides a hot-rolled steel strip product comprising a composition consisting of, in terms of weight percentages (wt. %): C 0.14 - 0.35, preferably 0.17 - 0.31, more preferably 0.20 - 0.28 Si 0 - 0.5, preferably 0.01 - 0.50, more preferably 0.03 - 0.25 Mn 0.05 - 0.40, preferably 0.05 - 0.30 Al 0 - 0.1, preferably 0 - 0.08 Cu 0.1 - 0.4, preferably 0.10 - 0.35 Ni 0.2 - 0.9, preferably 0.3 - 0.8, more preferably 0.3 - 0.7 Cr 0.2 - 0.9, preferably 0.3 - 0.8, more preferably 0.3 - 0.7 Mo 0 - 0.2, preferably 0 - 0.1 Nb 0 - 0.005 Ti 0 - 0.035 V 0 - 0.05 B 0.0005 - 0.0050, preferably 0.0008 - 0.0040 P
  • the steel product has a low content of Mn, which is important for improving impact toughness and bendability.
  • the levels of Cr and Ni are set to improve hardenability.
  • the level of Ni is further set to improve impact toughness and formability.
  • the level of Nb should be restricted to the lowest possible to increase formability or bendability of the steel product. Elements such as Nb may be present as residual contents that are not purposefully added.
  • residual contents are controlled quantities of alloying elements, which are not considered to be impurities.
  • a residual content as normally controlled by an industrial process does not have an essential effect upon the alloy.
  • the present invention provides a method for manufacturing hot-rolled steel strip product comprising the following steps of - providing a steel slab consisting of, in terms of weight percentages (wt. %): C 0.14 - 0.35, preferably 0.17 - 0.31, more preferably 0.20 - 0.28 Si 0 - 0.5, preferably 0.01 - 0.50, more preferably 0.03 - 0.25 Mn 0.05 - 0.40, preferably 0.05 - 0.30 Al 0 - 0.1, preferably 0 - 0.08 Cu 0.1 - 0.4, preferably 0.10 - 0.35 Ni 0.2 - 0.9, preferably 0.3 - 0.8, more preferably 0.3 - 0.7 Cr 0.2 - 0.9, preferably 0.3 - 0.8, more preferably 0.3 - 0.7 Mo 0 - 0.2, preferably 0 - 0.1 Nb 0 - 0.005 Ti 0 - 0.035 V 0 - 0.05 B 0.0005 - 0.0050,
  • a step of temper annealing is performed on the direct quenched product at a temperature in the range of 150 °C - 250 °C.
  • the step of temper annealing is not required according to the present invention.
  • the steel product is a steel strip having a thickness of 10 mm or less, preferably 8 mm or less.
  • the obtained steel product has a microstructure comprising, in terms of volume percentages (vol. %), at least 90 vol. % martensite, preferably at least 95 vol. % martensite, and more preferably at least 98 vol. % martensite, measured from 1 ⁇ 4 thickness of the steel strip product.
  • the martensitic structure may be untempered, autotempered and/or tempered.
  • the microstructure also comprises retained austenite, bainite, ferrite and/or cementite.
  • the obtained steel product has a prior austenite grain size of 50 ⁇ m or less, preferably 30 ⁇ m or less, more preferably 20 ⁇ m or less, measured from 1 ⁇ 4 thickness of the steel strip product.
  • the aspect ratio of a prior austenite grain structure is one of the factors affecting a steel product's impact toughness and bendability.
  • the prior austenite grain structure should have an aspect ratio of at least 1.5, preferably at least 2, and more preferably at least 3.
  • the prior austenite grain structure should have an aspect ratio of 7 or less, preferably 5 or less, and more preferably 1.5 or less.
  • the obtained steel product according to the present invention has a prior austenite grain structure with an aspect ratio in the range of 1.5 - 7, preferably 1.5 - 5, and more preferably 2 - 5, which ensures that a good balance of excellent impact toughness and excellent bendability can be achieved.
  • the steel product has a good balance of high hardness and excellent mechanical properties such as impact strength and formability/bendability.
  • the steel product has at least one of the following mechanical properties:
  • the steel product exhibits excellent bendability or formability.
  • the steel product has a minimum bending radius of 3.2 t or less in a measurement direction longitudinal to the rolling direction wherein the bending axis is longitudinal to rolling direction; a minimum bending radius of 2.5 t or less in a measurement direction transversal to the rolling direction wherein the bending axis is transversal to rolling direction; and wherein t is the thickness of the steel strip product.
  • steel is defined as an iron alloy containing carbon (C).
  • Brinell hardness is a designation of hardness of steel.
  • the Brinell hardness test is performed by pressing a spherical tungsten carbide ball with a diameter of 10 mm against a clean prepared surface of a metal sheet using a 3000 kilogram force, producing an impression, measured and given a special numerical value.
  • a spherical tungsten carbide ball with a diameter of 5 mm and a load of 750 kilogram force are applied to test samples with thinner gauges, e.g. 3 mm in thickness.
  • gauge refers generally to a measure of the thickness of a metal sheet.
  • yield strength (YS, R p 0.2) refers to 0.2 % offset yield strength defined as the amount of stress that will result in a plastic strain of 0.2 %.
  • total elongation refers to the percentage by which the material can be stretched before it breaks; a rough indicator of formability, usually expressed as a percentage over a fixed gauge length of the measuring extensometer. Two common gauge lengths are 50 mm (A50) and 80 mm (A80).
  • minimum bending radius (R i ) is used to refer to the minimum radius of bending that can be applied to a test sheet without occurrence of cracks.
  • HAZ heat-affected zone
  • the alloying content of steel together with the processing parameters determines the microstructure which in turn determines the mechanical properties of the steel.
  • Alloy design is one of the first issues to be considered when developing a steel product with targeted mechanical properties.
  • chemical composition according to the present invention is described in more details, wherein % of each component refers to weight percentage.
  • Carbon C is used in the range of 0.14 % to 0.35 %.
  • C alloying increases strength of steel by solid solution strengthening, and hence C content determines the strength level.
  • C is used in the range of 0.14 % to 0.35 % depending on targeted hardness. If the carbon content is less than 0.14%, it is difficult to achieve a Brinell hardness of more than 420 HBW. C is also an austenite stabilizing element. However, C has detrimental effects on weldability, impact toughness, formability or bendability, and resistance to stress corrosion cracking. Therefore, C content is set to not more than 0.35 %.
  • C is used in the range of 0.17 % to 0.31 %, and more preferably 0.20 % to 0.28 %.
  • Silicon Si is used in an amount of 0.5 % or less.
  • Si is added to the composition to facilitate formation of a protective oxide layer under corrosive climate conditions, which provides good resistance against climatic corrosion and increases the durability of a paint layer that is easily damaged or removed from machines surfaces due to wear.
  • Si is effective as a deoxidizing or killing agent that can remove oxygen from the melt during a steelmaking process.
  • Si alloying enhances strength by solid solution strengthening, and enhances hardness by increasing austenite hardenability. Also the presence of Si can stabilize retained austenite.
  • silicon content of higher than 0.5 % may unnecessarily increase carbon equivalent (CE) value thereby weakening the weldability.
  • CE carbon equivalent
  • Si is used in the range of 0.01 % to 0.50 %, and more preferably 0.03 % to 0.25 %.
  • Manganese Mn is used in the range of 0.05 % to 0.40 %.
  • Mn alloying lowers martensite start temperature (M s ) and martensite finish temperature (M f ), which can suppress autotempering of martensite during quenching. Reduced autotempering of martensite leads to higher internal stresses that may enhance the risk for quench-induced cracking or distortion of shape. Although a lower degree of autotempered martensitic microstructures is beneficial to higher hardness, its negative effects on impact strength should not be underestimated.
  • Mn alloying enhances strength by solid solution strengthening, and enhances hardness by increasing austenite hardenability. However, if the Mn content is too high, hardenability of the steel will increase at the expense of impact toughness. Excessive Mn alloying may also lead to C-Mn segregation and formation of MnS, which could induce formation of initiation sites for pitting corrosion and stress corrosion cracking.
  • Mn is used in an amount of at least 0.05 % to ensure hardenability, but not more than 0.40 % to avoid the harmful effects as described above and to ensure excellent mechanical properties such as impact strength and bendability.
  • a low level of Mn is used in the range of 0.05 % to 0.30 % to further improve the bendability.
  • Aluminum Al is used in the range of 0.1 % or less.
  • Al is effective as a deoxidizing or killing agent that can remove oxygen from the melt during a steelmaking process.
  • Al removes N by forming stable AIN particles and provides grain refinement, which is beneficial to high toughness.
  • Al stabilizes retained austenite.
  • an excess of Al may increase non-metallic inclusions thereby deteriorating cleanliness.
  • Al is used in the range of 0.08 % or less.
  • Copper Cu is used in the range of 0.1 % to 0.4 %.
  • Cu is added to the composition to facilitate formation of a protective oxide layer under corrosive climate conditions, which provides good resistance against climatic corrosion and increases the durability of a paint layer that is easily damaged or removed from machines surfaces due to wear.
  • Cu may promote formation of low carbon bainitic structures, cause solid solution strengthening and contribute to precipitation strengthening.
  • Cu may also have beneficial effects of inhibiting stress corrosion cracking. When added in excessive amounts, Cu deteriorates field weldability and the heat affected zone (HAZ) toughness. Therefore, the upper limit of Cu is set to 0.4 %.
  • Cu is used in the range of 0.10 % to 0.35 %.
  • Nickel Ni is used in the range of 0.2 % to 0.9 %.
  • Ni is used to avoid quench induced cracking and also to improve toughness and formability.
  • Ni is an alloying element that improves austenite hardenability thereby increasing strength with no or marginal loss of impact toughness and/or heat-affected zone (HAZ) toughness.
  • HZ heat-affected zone
  • Ni also improves surface quality thereby preventing pitting corrosion, i.e. initiation site for stress corrosion cracking.
  • Ni is added to the composition to facilitate formation of a protective oxide layer under corrosive climate conditions, which provides good resistance against climatic corrosion and increases the durability of a paint layer that is easily damaged or removed from machines surfaces due to wear.
  • nickel contents of above 0.9 % would increase alloying costs too much without significant technical improvement.
  • An excess of Ni may produce high viscosity iron oxide scales which deteriorate surface quality of the steel product.
  • Higher Ni contents also have negative impacts on weldability due to increased CE value and cracking sensitivity coefficient.
  • Ni is preferably used in the range of 0.3 % to 0.8 %, and more preferably 0.3 % to 0.7 %.
  • Chromium Cr is used in the range of 0.2 % to 0.9 %.
  • Cr is added to the composition to facilitate formation of a protective oxide layer under corrosive climate conditions, which provides good resistance against climatic corrosion and increases the durability of a paint layer that is easily damaged or removed from machines surfaces due to wear.
  • Cr alloying provides better resistance against pitting corrosion thereby preventing stress corrosion cracking at an early stage.
  • mid-strength carbide forming element Cr increases the strength of both the base steel and weld with marginal expense of impact toughness.
  • Cr alloying also enhances strength and hardness by increasing austenite hardenability.
  • HZ heat-affected zone
  • Cr is used in the range of 0.3 % to 0.8 %, and more preferably 0.3 % to 0.7 %.
  • Molybdenum Mo is used in the range of 0.2 % or less.
  • Mo alloying improves impact strength, low-temperature toughness and tempering resistance.
  • the presence of Mo enhances strength and hardness by increasing austenite hardenability.
  • Mo can be added to the composition to provide hardenability in place of Mn.
  • B alloying Mo is usually required to ensure the effectiveness of B.
  • Mo is not an economically acceptable alloying element. If Mo is used in an amount of above 0.2 % toughness may be deteriorated thereby increasing the risk of brittleness. An excessive amount of Mo may also reduce the effect of B.
  • the inventors have noticed that Mo alloying retards recrystallization of austenite thereby increasing the aspect ratio of a prior austenite grain structure. Therefore, the level of Mo content should be carefully controlled to prevent excessive elongation of the prior austenite grains which may deteriorate bendability of the steel product.
  • Mo is used in the range of 0.1 % or less.
  • Niobium Nb is used in an amount of 0.005 % or less.
  • Nb forms carbides NbC and carbonitrides Nb(C,N).
  • Nb is considered to be the major grain refining element.
  • Nb contributes to strengthening and toughening of steels.
  • Nb addition should be limited to 0.005 % since an excess of Nb deteriorates bendability, in particular when direct quenching is applied and/or when Mo is present in the composition.
  • Nb can be harmful for heat-affected zone (HAZ) toughness since Nb may promote the formation of coarse upper bainite structure by forming relatively unstable TiNbN or TiNb(C,N) precipitates.
  • the level of Nb should be restricted to the lowest possible to increase formability or bendability of the steel product.
  • Titanium Ti is used in an amount of 0.035 % or less.
  • TiC precipitates are able to deeply trap a significant amount of hydrogen H, which decreases the H diffusivity in the materials and removes some of the detrimental H from the microstructure to prevent stress corrosion cracking.
  • Ti is also added to bind free N that is harmful to toughness by forming stable TiN that together with NbC can efficiently prevent austenite grain growth in the reheating stage at high temperatures.
  • TiN precipitates can further prevent grain coarsening in the heat-affected zone (HAZ) during welding thereby improving toughness.
  • HZ heat-affected zone
  • TiN formation suppresses BN precipitation, thereby leaving B free to make its contribution to hardenability.
  • Ti content is too high, coarsening of TiN and precipitation hardening due to TiC develop and toughness may be deteriorated. Therefore, it is necessary to restrict Ti so that it does not exceed 0.035%.
  • Vanadium V is used in an amount of 0.05 % or less.
  • V has substantially the same but smaller effects as Nb.
  • V4C3 precipitates are able to deeply trap a significant amount of hydrogen H, which decreases the H diffusivity in the materials and removes some of the detrimental H from the microstructure to prevent hydrogen induced cracking (HIC).
  • H hydrogen induced cracking
  • V is a strong carbide and nitride former, but V(C,N) can also form and its solubility in austenite is higher than that of Nb or Ti.
  • V alloying has potential for dispersion and precipitation strengthening, because large quantities of V are dissolved and available for precipitation in ferrite.
  • an addition of more than 0.05 % V has negative effects on weldability, hardenability and alloying cost.
  • Boron B is used in the range of 0.0005 % to 0.0050 %.
  • B is a well-established microalloying element to increase hardenability. Boron can be added to retard phosphorus segregation to grain boundaries thereby reducing embrittlement during welding in the heat-affected zone (HAZ). Effective B alloying requires the presence of Ti to prevent formation of BN. In the presence of B, Ti content can be lowered to be less than 0.02%, which is beneficial for toughness. However, hardenability deteriorates if the B content exceeds 0.005 %.
  • B is used in the range of 0.0008 % to 0.0040 %.
  • Calcium Ca is used in an amount of 0.01 % or less.
  • Ca addition during a steelmaking process is for refining, deoxidation, desulphurization, and control of shape, size and distribution of oxide and sulphide inclusions.
  • Ca is usually added to improve subsequent coating.
  • an excessive amount of Ca should be avoided to achieve clean steel thereby preventing the formation of calcium sulfide (CaS) or calcium oxide (CaO) or mixture of these (CaOS) that may deteriorate the mechanical properties such as bendability and stress corrosion cracking (SCC) resistance.
  • CaS calcium sulfide
  • CaO calcium oxide
  • SCC stress corrosion cracking
  • Ca is used in an amount of 0.005 % or less, and more preferably 0.003 % or less to ensure excellent mechanical properties such as impact strength and bendability.
  • Unavoidable impurities can be phosphor P, sulfur S and nitrogen N. Their content in terms of weight percentages (wt. %) is preferably defined as follows: P 0 - 0.025, preferably 0 - 0.020 S 0 - 0.008, preferably 0 - 0.005 N 0 - 0.01, preferably 0 - 0.005
  • the steel product with the targeted mechanical properties is produced in a process that determines a specific microstructure which in turn dictates the mechanical properties of the steel product.
  • the first step is to provide a steel slab by means of, for instance a process of continuous casting, also known as strand casting.
  • the steel slab is heated to the austenitizing temperature of 1150 - 1300 °C, and thereafter subjected to a temperature equalizing step that may take 30 to 150 minutes.
  • the reheating and equalizing steps are important for controlling the austenite grain growth. An increase in the heating temperature can cause dissolution and coarsening of alloy precipitates, which may result in abnormal grain growth.
  • the final steel product has a prior austenite grain size of 50 ⁇ m or less, preferably 30 ⁇ m or less, more preferably 20 ⁇ m or less, measured from 1 ⁇ 4 thickness of the steel strip product.
  • the slab is hot rolled to the desired thickness at a temperature in the range of Ar 3 to 1250°C, wherein the finish rolling temperature (FRT) is in the range of 800 °C to 960 °C, preferably 870°C - 940°C, more preferably 880°C - 930°C.
  • FRT finish rolling temperature
  • the aspect ratio of a prior austenite grain structure is one of the factors affecting a steel product's impact toughness and bendability.
  • the prior austenite grain structure should have an aspect ratio of at least 1.5, preferably at least 2, and more preferably at least 3.
  • the prior austenite grain structure should have an aspect ratio of 7 or less, preferably 5 or less, and more preferably 1.5 or less.
  • a desired aspect ratio of prior austenite grains can be achieved by adjusting a number of parameters such as finish rolling temperature, strain/deformation, strain rate, and/or alloying with the elements such as Mo that retard recrystallization of austenite.
  • the obtained steel product according to the present invention has a prior austenite grain structure with an aspect ratio in the range of 1.5 - 7, preferably 1.5 - 5, and more preferably 2 - 5, which ensures that a good balance of excellent impact toughness and excellent bendability can be achieved.
  • the obtained steel strip product has a thickness of 10 mm or less, preferably 8 mm or less.
  • the hot-rolled steel strip product is direct quenched to a cooling end and coiling temperature of 450 °C or less, preferably 250 °C or less, more preferably 150 °C or less, and even more preferably 100 °C or less.
  • the cooling rate is at least 30 °C/s.
  • the direct quenched steel strip product is coiled at temperature of 450 °C or less, preferably 250 °C or less, more preferably 150 °C or less, and even more preferably 100 °C or less.
  • the obtained steel strip product has a microstructure comprising, in terms of volume percentages (vol. %), at least 90 vol. % martensite, preferably at least 95 vol. % martensite, and more preferably at least 98 vol. % martensite, measured from 1 ⁇ 4 thickness of the steel strip product.
  • the martensitic structure may be untempered, autotempered and/or tempered.
  • the microstructure comprises 1 vol. % or less retained austenite, and more preferably 0.5 vol. % or less retained austenite.
  • the microstructure also comprises bainite, ferrite, pearlite and/or cementite.
  • an extra step of temper annealing is performed at a temperature in the range of 150 °C - 250 °C.
  • the steel strip product has a good balance of hardness and other mechanical properties such as excellent impact strength and excellent formability/bendability.
  • the steel strip product has a high Brinell hardness in the range of 420 - 580 HBW, preferably 450 - 550 HBW, more preferably 460 - 530 HBW, and even more preferably 470 - 530 HBW.
  • the steel strip product with high hardness has a Charpy-V impact toughness of at least 50 J/cm 2 at a temperature of -40 °C thereby fulfilling the conventional impact strength requirements.
  • the steel strip product exhibits excellent bendability or formability.
  • the steel product has a minimum bending radius (R i ) of 3.2 t or less in a measurement direction longitudinal to the rolling direction wherein the bending axis is longitudinal to rolling direction; a minimum bending radius (R i ) of 2.5 t or less in a measurement direction transversal to the rolling direction wherein the bending axis is transversal to rolling direction; and wherein t is the thickness of the steel strip product.
  • Steel types A - C are the inventive compositions according to the present disclosure.
  • Steel types D and E are comparative compositions which comprise a relatively high Mn content of 1.20 wt. % and 1.19 wt. % respectively (Table 1).
  • Microstructure can be characterized from SEM micrographs and the volume fraction can be determined using point counting or image analysis method.
  • the microstructures of the tested inventive examples no. 1 - 3 all have a main phase of martensite in an amount of at least 90 vol. %.
  • the Brinell hardness test is performed by pressing a spherical tungsten carbide ball with a diameter of 10 mm against a clean prepared surface of the steel strip samples with a thickness of 6 mm using a 3000 kilogram force, producing an impression, measured and given a special numerical value.
  • a spherical tungsten carbide ball with a diameter of 5 mm and a load of 750 kilogram force are applied for the strip samples with a thickness of 3 mm.
  • the measurement is done perpendicular to the upper surface of the steel sheet at 10 - 15 % depth from the steel surface.
  • each one of the inventive examples no. 1 - 3 exhibits a Brinell harness in the range of 467 - 489 HBW.
  • the comparative examples no. 4 exhibits a Brinell harness of 485 HBW while the comparative example no. 5 exhibits a Brinell harness of 502 HBW.
  • the impact toughness values at -40 °C are obtained by Charpy V-notch tests according to the ISO 148 standard.
  • Each one of the inventive examples no. 1 - 3 has a Charpy-V impact toughness in the range of 78 - 118 J/cm 2 at a temperature of -40 °C if the measurement direction is longitudinal to the rolling direction.
  • Each one of the inventive examples no. 1 - 3 has a Charpy-V impact toughness in the range of 65 - 90 J/cm 2 at a temperature of -40 °C if the measurement direction is transversal to the rolling direction.
  • the impact toughness of the inventive examples no. 1 - 3 is improved compared to the comparative examples no. 4 and 5.
  • Elongation was determined according ISO 6892 standard using longitudinal specimens.
  • the mean value of total elongation (A80) of the inventive examples no. 1, 2 and 3 is 4.5, 7.6 and 7.7 respectively (Table 3).
  • the comparative examples no. 4 and 5 have better elongation values than the inventive examples no. 1 - 3 at the expense of Charpy-V impact toughness and bendability.
  • the bend test consists of subjecting a test piece to plastic deformation by three-point bending, with one single stroke, until a specified angle 90° of the bend is reached after unloading.
  • the inspection and assessment of the bends is a continuous process during the whole test series. This is to be able to decide if the punch radius (R) should be increased, maintained or decreased.
  • the limit of bendability (R/t) for a material can be identified in a test series if a minimum of 3 m bending length, without any defects, is fulfilled with the same punch radius (R) both longitudinally and transversally. Cracks, surface necking marks and flat bends (significant necking) are registered as defects.
  • each one of the inventive examples no. 1 - 3 has a minimum bending radius (R i ) of 2.8 t or less in a measurement direction longitudinal to the rolling direction; a minimum bending radius (R i ) of 2.0 t or less in a measurement direction transversal to the rolling direction; and wherein t is the thickness of the steel strip product (Table 3).
  • the comparative examples no. 4 and 5 exhibit a minimum bending radius (R i ) of 3.7 t and 3.3 t respectively in a measurement direction longitudinal to the rolling direction, and a minimum bending radius (R i ) of 3.0 t and 2.7 t respectively in a measurement direction transversal to the rolling direction (Table 3).
  • Yield strength was determined according ISO 6892 standard using longitudinal specimens.
  • Each one of the inventive examples no. 1 - 3 has a mean value of yield strength (R p 0.2) in the range of 1310 MPa to 1413 MPa measured in the longitudinal direction (Table 3).
  • the comparative examples no. 4 and 5 have a mean value of yield strength (R p 0.2) of 1375 MPa and 1397 MPa respectively, measured in the longitudinal direction (Table 3).
  • Ultimate tensile strength (R m ) was determined according ISO 6892 standard using longitudinal specimens.
  • Each one of the inventive examples no. 1 - 3 has a mean value of ultimate tensile strength (R m ) in the range of 1511 MPa to 1609 MPa, measured in the longitudinal direction (Table 3).
  • the comparative examples no. 4 and 5 have a mean value of ultimate tensile strength (R m ) of 1617 MPa and 1654 MPa respectively, measured in the longitudinal direction (Table 3).
  • Table 1 Chemical compositions (wt. %).

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2023067544A1 (fr) * 2021-10-20 2023-04-27 Tata Steel Limited Acier laminé à chaud faiblement allié de haute dureté et son procédé de fabrication
EP4180544A1 (fr) * 2021-11-11 2023-05-17 SSAB Technology AB Procédé de bande d'acier laminée à chaud et son procédé de production

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AU2019363613A1 (en) 2018-10-26 2021-05-20 Oerlikon Metco (Us) Inc. Corrosion and wear resistant nickel based alloys
WO2023080629A1 (fr) 2021-11-02 2023-05-11 주식회사 엘지에너지솔루션 Matériau actif de cathode de batterie secondaire
CN114774772B (zh) * 2022-03-07 2023-10-31 江阴兴澄特种钢铁有限公司 一种耐腐蚀500hb马氏体耐磨钢板及其生产方法
CN115058572B (zh) * 2022-06-13 2023-07-04 北京科技大学 一种添加中间层的不锈钢/碳钢层状复合板及其制备方法

Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2009030093A (ja) * 2007-07-26 2009-02-12 Jfe Steel Kk 耐低温焼戻し脆化割れ特性に優れた耐磨耗鋼板
CN102199737A (zh) 2010-03-26 2011-09-28 宝山钢铁股份有限公司 一种600hb级耐磨钢板及其制造方法
JP4874434B1 (ja) * 2010-02-15 2012-02-15 新日本製鐵株式会社 厚鋼板の製造方法
CN102392186A (zh) 2011-11-07 2012-03-28 南京钢铁股份有限公司 一种hb500级低锰耐磨钢板的制造方法
EP2578705A1 (fr) * 2010-06-03 2013-04-10 Nippon Steel & Sumitomo Metal Corporation Procédé de production d'un tuyau en acier pour coussin de sécurité gonflable
EP2695960A1 (fr) 2011-03-29 2014-02-12 JFE Steel Corporation Tôle d'acier résistant à l'abrasion qui présente une excellente résistance à une fissuration par corrosion sous tension et procédé de production de cette dernière
CN103820717A (zh) 2014-01-28 2014-05-28 莱芜钢铁集团有限公司 钢板及其制备方法
EP2778239A1 (fr) * 2013-03-14 2014-09-17 Tenaris Coiled Tubes, LLC Matériau haute performance pour des applications de tubage enroulé et son procédé de production
WO2015007723A1 (fr) * 2013-07-16 2015-01-22 Rautaruukki Oyj Procécé de fabrication de produit de bande d'acier recuit après galvanisation pour formage à la presse à chaud, procédé de fabrication de composant d'acier pressé à chaud et produit de bande d'acier recuit après galvanisation

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101270439A (zh) * 2007-03-23 2008-09-24 宝山钢铁股份有限公司 一种高强度热轧防弹钢板及其制造方法
CN101660108A (zh) * 2009-10-16 2010-03-03 江苏省沙钢钢铁研究院有限公司 非调质针状组织高强度低屈强比耐候钢及其生产方法
FI20115702L (fi) * 2011-07-01 2013-01-02 Rautaruukki Oyj Menetelmä suurlujuuksisen rakenneteräksen valmistamiseksi ja suurlujuuksinen rakenneteräs
AU2013204206B2 (en) * 2012-10-19 2016-09-15 Bluescope Steel Limited Steel Plate
SI2789699T1 (sl) * 2013-08-30 2017-06-30 Rautaruukki Oyj Utrjeni vroče valjani jekleni proizvod in metoda za proizvodnjo le-tega
EP3097214B1 (fr) * 2014-01-24 2021-02-24 Rautaruukki Oyj Produit de bande d'acier très haute résistance laminé à chaud
JP6394378B2 (ja) * 2014-12-26 2018-09-26 新日鐵住金株式会社 耐摩耗鋼板およびその製造方法
ES2818195T5 (es) * 2015-12-15 2023-11-30 Tata Steel Ijmuiden Bv Tira de acero galvanizado por inmersión en caliente de alta resistencia
US10174398B2 (en) * 2016-02-22 2019-01-08 Nucor Corporation Weathering steel
CA3017286C (fr) * 2016-04-19 2021-01-05 Jfe Steel Corporation Tole d'acier resistante a l'abrasion et procede de production de tole d'acier resistante a l'abrasion
BR112018070771B1 (pt) * 2016-04-19 2023-10-31 Jfe Steel Corporation Placa de aço resistente à abrasão e seu método de produção
WO2018138270A1 (fr) * 2017-01-26 2018-08-02 Ssab Technology Ab Acier durci par trempe
EP3597784B1 (fr) * 2017-03-13 2021-03-31 JFE Steel Corporation Tôle d'acier résistante à l'abrasion et son procédé de production

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2009030093A (ja) * 2007-07-26 2009-02-12 Jfe Steel Kk 耐低温焼戻し脆化割れ特性に優れた耐磨耗鋼板
JP4874434B1 (ja) * 2010-02-15 2012-02-15 新日本製鐵株式会社 厚鋼板の製造方法
CN102199737A (zh) 2010-03-26 2011-09-28 宝山钢铁股份有限公司 一种600hb级耐磨钢板及其制造方法
EP2578705A1 (fr) * 2010-06-03 2013-04-10 Nippon Steel & Sumitomo Metal Corporation Procédé de production d'un tuyau en acier pour coussin de sécurité gonflable
EP2695960A1 (fr) 2011-03-29 2014-02-12 JFE Steel Corporation Tôle d'acier résistant à l'abrasion qui présente une excellente résistance à une fissuration par corrosion sous tension et procédé de production de cette dernière
CN102392186A (zh) 2011-11-07 2012-03-28 南京钢铁股份有限公司 一种hb500级低锰耐磨钢板的制造方法
EP2778239A1 (fr) * 2013-03-14 2014-09-17 Tenaris Coiled Tubes, LLC Matériau haute performance pour des applications de tubage enroulé et son procédé de production
WO2015007723A1 (fr) * 2013-07-16 2015-01-22 Rautaruukki Oyj Procécé de fabrication de produit de bande d'acier recuit après galvanisation pour formage à la presse à chaud, procédé de fabrication de composant d'acier pressé à chaud et produit de bande d'acier recuit après galvanisation
CN103820717A (zh) 2014-01-28 2014-05-28 莱芜钢铁集团有限公司 钢板及其制备方法

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WO2023067544A1 (fr) * 2021-10-20 2023-04-27 Tata Steel Limited Acier laminé à chaud faiblement allié de haute dureté et son procédé de fabrication
EP4180544A1 (fr) * 2021-11-11 2023-05-17 SSAB Technology AB Procédé de bande d'acier laminée à chaud et son procédé de production
WO2023083898A1 (fr) * 2021-11-11 2023-05-19 Ssab Technology Ab Produit en bande d'acier laminée à chaud et son procédé de production

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JP2022528420A (ja) 2022-06-10
KR20210149123A (ko) 2021-12-08
BR112021019860A2 (pt) 2021-12-07
WO2020201437A1 (fr) 2020-10-08
SI3719148T1 (sl) 2023-06-30
CN113785079B (zh) 2024-04-05
CN113785078A (zh) 2021-12-10
CA3135141A1 (fr) 2020-10-08
BR112021019865A2 (pt) 2021-12-07
WO2020201438A1 (fr) 2020-10-08
EP3719149B1 (fr) 2023-03-22
EP3719148B1 (fr) 2023-01-25
EP3719148A1 (fr) 2020-10-07
US20220177996A1 (en) 2022-06-09
CN113785079A (zh) 2021-12-10
PL3719148T3 (pl) 2023-05-08
CA3135144A1 (fr) 2020-10-08
US20220177997A1 (en) 2022-06-09
CN113785078B (zh) 2023-10-27

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