EP3561106A1 - Matériau d'acier à paroi épaisse doté d'une résistance à la traction de 450 mpa et d'une excellente résistance à la fissuration induite par hydrogène, et procédé de fabrication d'un tel matériau d'acier à paroi épaisse - Google Patents

Matériau d'acier à paroi épaisse doté d'une résistance à la traction de 450 mpa et d'une excellente résistance à la fissuration induite par hydrogène, et procédé de fabrication d'un tel matériau d'acier à paroi épaisse Download PDF

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EP3561106A1
EP3561106A1 EP17882598.0A EP17882598A EP3561106A1 EP 3561106 A1 EP3561106 A1 EP 3561106A1 EP 17882598 A EP17882598 A EP 17882598A EP 3561106 A1 EP3561106 A1 EP 3561106A1
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Prior art keywords
steel plate
heavy
less
wall steel
induced cracking
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German (de)
English (en)
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EP3561106A4 (fr
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Seong-Ung KOH
Yoen-Jung PARK
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Posco Holdings Inc
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Posco Co Ltd
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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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C21D1/26—Methods of annealing
    • C21D1/28—Normalising
    • 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
    • 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
    • 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
    • C22C38/06—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
    • C22C38/12—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
    • C22C38/40—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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the present disclosure relates to a heavy-wall steel plate having excellent resistance to hydrogen induced cracking, and a method for manufacturing the same, and, in particular, to a normalizing heat treated heavy-wall steel plate having a thickness of 40 mm or more and having a tensile strength of 450 MPa, and a method for manufacturing the same.
  • a heavy-wall steel plate for guaranteeing hydrogen induced cracking according to American Petroleum Institute (API) standard has been used for line pipe, process pipe, or the like, and the required properties and manufacturing process of a steel material has been used determined, depending on the usage environment.
  • API American Petroleum Institute
  • the manufacturing process of a steel material requires a heat treatment process such as a normalizing process, a quenching/tempering process, or the like.
  • a heat treatment steel plate requires a normalizing steel material.
  • the normalizing steel material is generally low in strength due to the characteristics of the air-cooling material, and when the content of the alloying elements such as C, Mn, and the like, increases in order to facilitate an increase in strength, the resistance to hydrogen induced cracking may decrease sharply.
  • the reason is that the content of pearlite in the steel plate increases with the addition of C, Mn, and the like, and the resistance to hydrogen induced cracking decreases sharply over a certain percentage of the pearlite fraction.
  • the resistance to hydrogen induced cracking is reduced after the tubing of the steel pipe due to the characteristics of the normalized steel material, the requirements for resistance to hydrogen induced cracking have become stricter in recent years.
  • Korean Patent Publication No. 2004-0021117 proposes a steel material for a pressure vessel having a tensile strength of 600 MPa, which is excellent in toughness and used for materials such as boilers of a power plant, pressure vessels, or the like.
  • the steel material for a pressure vessel proposed by the Patent Publication has a composition comprising, by weight, carbon (C): 0.08% to 0.16%, silicon (Si): 0.1% to 0.4%, manganese (Mn): 0.8% to 1.8%, molybdenum (Mo): 0.2% to 0.8%, nickel (Ni): 0.3% to 0.8%, boron (B): 0.0005% to 0.003%, titanium (Ti): 0.005% to 0.025%, aluminum (Al): 0.01% to 0.08%, phosphorus (P): 0.010% or less, sulfur (S): 0.010% or less, nitrogen (N): 0.010% or less, a balance of iron (Fe), and other unavoidable impurities.
  • Korean Patent No. 0833070 proposes a heavy-wall steel plate for a pressure vessel excellent in resistance to hydrogen induced cracking while satisfying a tensile strength of 500 MPa.
  • a steel material having a composition comprising, by weight, carbon (C): 0.1% to 0.30%, silicon (Si): 0.15% to 0.40%, manganese (Mn): 0.6% to 1.2%, phosphorus (P): 0.035% or less, sulfur (S): 0.020% or less, aluminum (Al): 0.001% to 0.05%, chromium (Cr) : 0.35% or less, nickel (Ni): 0.5% or less, copper (Cu) : 0.5% or less, molybdenum (Mo) : 0.2% or less, vanadium (V) : 0.05% or less, niobium (Nb): 0.05% or less, calcium (Ca) :
  • Equation 1 Cu + Ni + Cr + Mo ⁇ 1.5%
  • Equation 2 Cr + Mo ⁇ 0.4%
  • Equation 3 V + Nb ⁇ 0.1%
  • Equation 4 Ca/S > 1.0, as relationships for components.
  • the above Patent relates to a method for manufacturing the steel material having a tensile strength of 500 MPa, as described above, comprising: reheating the steel material at 1050°C to 1250°C; performing a recrystallization controlled rolling operation of hot-rolling the reheated steel material at a temperature not lower than a non-recrystallization temperature; and performing a normalizing operation of heat treating the hot-rolled steel material at a temperature of 850°C to 950°C at 1.3 x t + (10 - 30 minutes) (where t denotes a thickness (mm) of a steel material).
  • the present disclosure is made to solve the above problems of the prior art, and it is an object of the present disclosure to optimize components in steel, a microstructure of the steel, a rolling operation, a cooling operation, and a heat treatment operation, to provide a normalizing heat treated heavy-wall steel plate having excellent resistance to hydrogen induced cracking, having a thickness of 40 mm or more and having a tensile strength of 450 MPa.
  • the heat treatment operation is performed at a temperature higher than that of a conventional normalizing heat treatment operation without including expensive precipitation-type elements such as Cr, Mo, V, etc., to provide a normalizing heat treated heavy-wall steel plate having excellent resistance to hydrogen induced cracking, and having a tensile strength of 450 MPa.
  • a heavy-wall steel plate having excellent resistance to hydrogen induced cracking includes, by weight, carbon (C): 0.03% to 0.06%, silicon (Si): 0.2% to 0.4%, manganese (Mn): 1.0% to 1.6%, phosphorus (P): 0.03% or less, sulfur (S): 0.003% or less, aluminum (Al): 0.06% or less, nitrogen (N): 0.01% or less, copper (Cu): 0.05% to 0.4%, nickel (Ni): 0.05% to 0.5%, calcium (Ca): 0.0005% to 0.003%, a balance of iron (Fe), and other unavoidable impurities, wherein a thickness of the heavy-wall steel plate is 40 mm or more, and tensile strength of the heavy-wall steel plate is 450 MPa or more.
  • the heavy-wall steel plate may further include niobium (Nb): 0.005% to 0.05% and titanium (Ti): 0.005% to 0.03%.
  • the heavy-wall steel plate may be a microstructure having a composite structure of ferrite and pearlite, and an area fraction of the pearlite may be less than 10%.
  • the heavy-wall steel plate may further include Al-Ca-based inclusions, and a minimum distance between Al-Ca-based inclusions having a diameter of 2 ⁇ m or more may be 100 ⁇ m or more in a rolling direction.
  • a method for manufacturing a heavy-wall steel plate having 450MPa-grade tensile strength and excellent resistance to hydrogen induced cracking includes:
  • a steel plate having excellent resistance to hydrogen induced cracking having a thickness of 40 mm or more, and having a tensile strength of 450 MPa, at relatively low manufacturing costs.
  • N is present in a solid-soluble state and N in a solid-soluble state has an adverse influence on low temperature toughness. Therefore, it is preferable to limit the content thereof to 0.01% or less.
  • Cu may be an element for improving the strength of ferrite through solid solution strengthening, and should be added in an amount of 0.05% or more. Since Cu is an element which causes cracks on the surface during a hot-rolling operation to hinder the surface quality, it is preferable to restrict the upper limit thereof to 0.4%.
  • Ni may be an element which improves the toughness of steel, and is preferably added in an amount of 0.05% or more, to reduce surface cracks generated during a hot-rolling operation of Cu-added steel.
  • the Ni content of 0.5% or more may increase price of the steel material. Therefore, it is preferable to restrict the upper limit thereof to 0.5%.
  • Ca may serve to spheroidize MnS inclusions.
  • MnS an inclusion having a relatively low melting point, produced in the central portion, may be stretched upon rolling to be present as a stretched inclusion in the central portion of steel.
  • MnS is present in a relatively large amount and partially dense, it may serve to decrease elongation when stretched in a thickness direction.
  • the added Ca may react with MnS to surround MnS, thereby interfering with the stretching of MnS.
  • Ca should be added in an amount 0.0005 wt % or more. Since Ca has high volatility and thus, has a relatively low yield, considering the load produced in the steel manufacturing process, it is preferable to restrict the upper limit thereof to 0.003 wt % or less.
  • the steel plate of the present disclosure may further include Fe and unavoidable impurities, and does not exclude the addition of other components in addition to the above-described components.
  • the steel plate of the present disclosure may additionally include other components in addition to the above-mentioned components in the composition of steel.
  • the steel having the above composition may have different microstructures depending on the contents of the elements, rolling operations, cooling conditions, and heat treatment conditions, and may affect strength and resistance to hydrogen induced cracking depending on the microstructure even with the same composition.
  • a microstructure of a normalized steel material of the present disclosure having excellent resistance to hydrogen induced cracking, having a thickness of 40 mm or more, and having a tensile strength of 450 MPa, will be described.
  • the steel plate having excellent resistance to hydrogen induced cracking may be a steel plate having a thickness of 40 mm or more, and may be a steel plate having excellent in resistance to hydrogen induced cracking while maintaining a relatively high strength of 450 MPa or more in tensile strength, regardless of its thickness.
  • a normalized steel has two phases of ferrite and pearlite as its matrix structure without adding excessive components.
  • a pearlite fraction in the matrix structure is 10% or more, since resistance to hydrogen induced cracking is lowered, the pearlite fraction in the present disclosure may be limited to less than 10%.
  • the Al-Ca-based inclusions may be a factor deteriorating the resistance to hydrogen induced cracking of low strength steel.
  • the minimum distance between Al-Ca-based inclusions having a diameter of 2 ⁇ m or more in a rolling direction is less than 100 ⁇ m, the resistance to hydrogen induced cracking may be deteriorated. It is preferable that a lower limit in the minimum distance between the Al-Ca-based inclusions having a diameter of 2 ⁇ m or more be limited to 100 ⁇ m.
  • a steel slab having the above-mentioned composition may be prepared, and, then, may be reheated in a temperature range of 1100°C to 1300°C.
  • the reheating process is an operation of heating the steel slab to a relatively high temperature, to hot-roll the steel slab.
  • the reheating temperature is higher than the upper limit of 1300°C defined by the present disclosure, the austenite crystal grains may be excessively coarsened to lower the strength of steel, and to generate scale defects.
  • the reheating temperature is less than 1100°C, re-solid soluble ratio of the alloying elements may decrease. Accordingly, in the present disclosure, the range of the reheating temperature is preferably limited to 1100°C to 1300°C, and more preferably 1100°C to 1180°C in terms of strength and toughness.
  • the heated slab may be hot-rolled such that the total rolling reduction thickness is less than 200 mm at a finish rolling temperature of 900°C or higher, so as to prepare a hot-rolled steel plate.
  • the finish rolling temperature is lower than 900°C
  • large Al-Ca-based inclusions may be divided in the rolling direction, such that a minimum distance between Al-Ca-based inclusions having a diameter of 2 ⁇ m or more is less than 100 ⁇ m. Therefore, since the resistance to hydrogen induced cracking in the steel may be rapidly deteriorated, it is preferable to hot-roll the heated slab that the total rolling reduction thickness in the present disclosure is limited to be less than 200 mm.
  • the crystal grains may be finer and the low-temperature toughness may be improved.
  • the total rolling reduction thickness of the slab is 200 mm or more, the Al-Ca-based inclusions of a normalizing steel material may be easily divided in the rolling direction during a rolling operation, such that a minimum distance between Al-Ca-based inclusions having a diameter of 2 ⁇ m or more is less than 100 ⁇ m. Therefore, since the resistance to hydrogen induced cracking in the steel may be rapidly deteriorated, it is preferable to hot-roll the heated slab that the total rolling reduction thickness in the present disclosure is limited to be 200 mm or less.
  • the hot-rolled steel plate may be cooled, preferably by air cooling. Since the steel material to be provided is subjected to a heat treatment after rolling, the cooling process is not an important process variable, but when the steel plate is water cooled from a relatively high temperature, it may cause shape deformation and productivity resistance of the steel plate.
  • the hot-rolled steel plate is subjected to a normalizing treatment in a temperature range of 1000°C to 1100°C.
  • the normalizing temperature refers to a temperature at which the cooled steel plate is reheated to the austenite region at a certain temperature or more after the hot-rolling operation, and an air cooling operation may perform after the heating operation.
  • the normalizing temperature may be performed directly on the Ar3 temperature. Since the normalizing temperature range proposed in this study is aimed at coarsening crystal grain through the austenite crystal grain growth, it may deviate from the normal normalizing temperature.
  • the austenite crystal grains when the normalizing temperature is less than 1000°C, the austenite crystal grains may be not sufficiently coarsened. Therefore, no sufficient quenchability may be secured at the time of the air cooling operation, and ferrite and pearlite formed at the time of the air cooling operation may not be completely transformed into austenite phase.
  • the normalizing temperature exceeds 1100°C, the austenite crystal grains may be excessively coarsened. Therefore, the low-temperature toughness may deteriorate and a high-temperature scale may be caused on the surface of the steel.
  • the range of the normalizing reheating temperature is preferably limited to 1000°C to 1100°C.
  • the steel types illustrated in the following Table 1 were prepared to produce steel plates according to the manufacturing process conditions illustrated in the following Table 2. Specifically, the steel slab having the composition illustrated in the following Table 1 was heated to the heating temperature illustrated in the following Table 2, rolled to the finish rolling temperature and the total rolling reduction thickness illustrated in the following Table 2, reheated to the reheating temperature illustrated in the following Table 2, and then air-cooled.
  • the pearlite area fraction and the distance between the Al-Ca-based inclusions were obtained by observing the microstructure of the steel plate, and the hydrogen induced cracking sensitivity (CLR) was tested according to the method specified by a National Association of Corrosion Engineers (NACE), and percentage of the length of the hydrogen induced cracking generated with respect to the entire length of the specimen.
  • CLR hydrogen induced cracking sensitivity

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
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EP17882598.0A 2016-12-22 2017-11-24 Matériau d'acier à paroi épaisse doté d'une résistance à la traction de 450 mpa et d'une excellente résistance à la fissuration induite par hydrogène, et procédé de fabrication d'un tel matériau d'acier à paroi épaisse Withdrawn EP3561106A4 (fr)

Applications Claiming Priority (2)

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KR1020160176896A KR101889189B1 (ko) 2016-12-22 2016-12-22 수소유기균열 저항성이 우수한 인장강도 450MPa급 후육 강재 및 그 제조방법
PCT/KR2017/013550 WO2018117449A1 (fr) 2016-12-22 2017-11-24 Matériau d'acier à paroi épaisse doté d'une résistance à la traction de 450 mpa et d'une excellente résistance à la fissuration induite par hydrogène, et procédé de fabrication d'un tel matériau d'acier à paroi épaisse

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CN110114490A (zh) 2019-08-09
KR101889189B1 (ko) 2018-08-16
US20190382865A1 (en) 2019-12-19
JP2020503445A (ja) 2020-01-30
WO2018117449A1 (fr) 2018-06-28
EP3561106A4 (fr) 2019-10-30
KR20180073256A (ko) 2018-07-02

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