CA3194605A1 - Hydrogen-induced cracking-resistant steel plate with thickness of > 200-250 mm for pressure vessel and method for manufacturing same - Google Patents
Hydrogen-induced cracking-resistant steel plate with thickness of > 200-250 mm for pressure vessel and method for manufacturing sameInfo
- Publication number
- CA3194605A1 CA3194605A1 CA3194605A CA3194605A CA3194605A1 CA 3194605 A1 CA3194605 A1 CA 3194605A1 CA 3194605 A CA3194605 A CA 3194605A CA 3194605 A CA3194605 A CA 3194605A CA 3194605 A1 CA3194605 A1 CA 3194605A1
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- Prior art keywords
- rolling
- steel plate
- temperature
- blank
- hydrogen
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 196
- 239000010959 steel Substances 0.000 title claims abstract description 196
- 239000001257 hydrogen Substances 0.000 title claims abstract description 76
- 229910052739 hydrogen Inorganic materials 0.000 title claims abstract description 76
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 title claims abstract description 73
- 238000005336 cracking Methods 0.000 title claims abstract description 53
- 238000000034 method Methods 0.000 title claims abstract description 52
- 238000004519 manufacturing process Methods 0.000 title claims description 57
- 238000005096 rolling process Methods 0.000 claims abstract description 143
- 238000010438 heat treatment Methods 0.000 claims abstract description 80
- 238000009749 continuous casting Methods 0.000 claims abstract description 59
- 230000008569 process Effects 0.000 claims abstract description 31
- 238000005496 tempering Methods 0.000 claims abstract description 24
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 24
- 238000001816 cooling Methods 0.000 claims abstract description 18
- 238000009792 diffusion process Methods 0.000 claims abstract description 14
- 239000000203 mixture Substances 0.000 claims abstract description 11
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 10
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 9
- 239000000126 substance Substances 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 8
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 8
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 150000001875 compounds Chemical class 0.000 claims description 68
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 36
- 238000005266 casting Methods 0.000 claims description 34
- 238000005204 segregation Methods 0.000 claims description 32
- 238000003723 Smelting Methods 0.000 claims description 30
- 238000003466 welding Methods 0.000 claims description 27
- 229910052786 argon Inorganic materials 0.000 claims description 18
- 230000007547 defect Effects 0.000 claims description 17
- 230000009467 reduction Effects 0.000 claims description 17
- 238000013329 compounding Methods 0.000 claims description 16
- 238000002791 soaking Methods 0.000 claims description 16
- 238000007664 blowing Methods 0.000 claims description 13
- 238000005516 engineering process Methods 0.000 claims description 13
- 239000007789 gas Substances 0.000 claims description 13
- 238000007670 refining Methods 0.000 claims description 12
- 238000001953 recrystallisation Methods 0.000 claims description 8
- 239000002893 slag Substances 0.000 claims description 7
- 238000010894 electron beam technology Methods 0.000 claims description 5
- 238000002360 preparation method Methods 0.000 claims 1
- 230000002035 prolonged effect Effects 0.000 claims 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 8
- 238000001514 detection method Methods 0.000 description 8
- RWSOTUBLDIXVET-UHFFFAOYSA-N Dihydrogen sulfide Chemical compound S RWSOTUBLDIXVET-UHFFFAOYSA-N 0.000 description 6
- 229910000037 hydrogen sulfide Inorganic materials 0.000 description 6
- 238000013461 design Methods 0.000 description 5
- 238000005242 forging Methods 0.000 description 5
- 238000005728 strengthening Methods 0.000 description 5
- 238000011161 development Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 230000035945 sensitivity Effects 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 125000004435 hydrogen atom Chemical group [H]* 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 230000033228 biological regulation Effects 0.000 description 2
- 230000005587 bubbling Effects 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 229910052729 chemical element Inorganic materials 0.000 description 1
- 239000003638 chemical reducing agent Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000004512 die casting Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 230000008676 import Effects 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000009434 installation Methods 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000005070 sampling Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
Classifications
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- 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
- C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/28—Normalising
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
- C21D1/60—Aqueous agents
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/84—Controlled slow cooling
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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
- C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
- C21D3/02—Extraction of non-metals
- C21D3/06—Extraction of hydrogen
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
- 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
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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
- 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
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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
- 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
- C21D8/0257—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
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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
- 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
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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
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
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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
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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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
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/18—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
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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
- C22C38/18—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
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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
- C22C38/18—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
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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
- C22C38/18—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
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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
- C22C38/18—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
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/62—Quenching devices
- C21D1/63—Quenching devices for bath quenching
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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- Metallurgy (AREA)
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- Physics & Mathematics (AREA)
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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Articles (AREA)
- Pressure Vessels And Lids Thereof (AREA)
Abstract
The present invention relates to a hydrogen-induced cracking-resistant steel plate with a thickness of > 200-250 mm for a pressure vessel. A chemical composition of the steel plate includes: C: 0.10-0.20%, Si: 0.15-0.40%, Mn: 0.95-1.35%, P: ? 0.005 %, S: ? 0.0008%, Cr: 0.10-0.30%, Ni: 0.25-0.40%, Mo: 0.08-0.12%, Alt: 0.02-0.05%, Nb: 0.01-0.02%, V: 0.01-0.03%, Ti: 0.01-0.02%, B: ? 0.0005%, and the rest being Fe and inevitable impurity elements. At the same time, the chemical composition has a carbon equivalent Ceq ? 0.45%, wherein Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15. In the present invention, by strictly controlling purity of molten steel and metallurgical quality of continuous casting blanks and adopting a high-temperature diffusion heating process, a high-permeability rolling process and a normalizing + water accelerated cooling + tempering heat treatment process, optimal matching of mechanical properties of the large-thickness hydrogen-induced cracking-resistant steel plate for the pressure vessel is realized, and the internal quality and hydrogen-induced cracking resistance of the steel plate are greatly improved.
Description
HYDROGEN-INDUCED CRACKING-RESISTANT STEEL PLATE WITH THICKNESS OF >
TECHNICAL FIELD
[01] The present invention relates to a hydrogen-induced cracking-resistant steel plate with a thickness of > 200-250 mm for a pressure vessel and a method for manufacturing the same, and in particular to a hydrogen-induced cracking-resistant extra-thick steel plate suitable for manufacturing of plate-welded pressure vessels and capable of being used in a wet hydrogen sulfide environment and a method for manufacturing the same. The present invention belongs to the technical field of iron-based alloy manufacturing.
BACKGROUND ART
TECHNICAL FIELD
[01] The present invention relates to a hydrogen-induced cracking-resistant steel plate with a thickness of > 200-250 mm for a pressure vessel and a method for manufacturing the same, and in particular to a hydrogen-induced cracking-resistant extra-thick steel plate suitable for manufacturing of plate-welded pressure vessels and capable of being used in a wet hydrogen sulfide environment and a method for manufacturing the same. The present invention belongs to the technical field of iron-based alloy manufacturing.
BACKGROUND ART
[02] There are mainly two methods of manufacturing thick-walled pressure vessels:
forge welding and plate welding. In comparison, plate welding has the advantages of short manufacturing cycle, relatively low cost, easy procurement of materials and uniform performance of plates. Therefore, replacing forge welding with plate welding is the long-term development direction of the pressure vessel industry in the future. In the manufacture of the pressure vessels, it is more difficult to manufacture a thick-walled plate-welded structure than a forge-welded structure. There are two main factors restricting the large-scale development of the plate-welded pressure vessels: one is that vessel manufacturers are limited by the capacity of tube section forming equipment; and the other is that the physical quality level and stability of domestic extra-thick steel plates are poor, which cannot fully meet manufacturing requirements of thick-walled vessels.
forge welding and plate welding. In comparison, plate welding has the advantages of short manufacturing cycle, relatively low cost, easy procurement of materials and uniform performance of plates. Therefore, replacing forge welding with plate welding is the long-term development direction of the pressure vessel industry in the future. In the manufacture of the pressure vessels, it is more difficult to manufacture a thick-walled plate-welded structure than a forge-welded structure. There are two main factors restricting the large-scale development of the plate-welded pressure vessels: one is that vessel manufacturers are limited by the capacity of tube section forming equipment; and the other is that the physical quality level and stability of domestic extra-thick steel plates are poor, which cannot fully meet manufacturing requirements of thick-walled vessels.
[03] In the 1990s, pressure vessels with a wall thickness greater than 150 mm were mostly manufactured by adopting a forge welding forming manner. In recent years, with upsizing of petrochemical installations and rapid development of the petrochemical industry, the demand for pressure vessels with the wall thickness greater than 150 mm has increased rapidly, and the manufacturing capacity of large forgings has been unable to meet market demands.
Therefore, it is imperative and imminent to replace the forgings with thick steel plates. With the improvement of smelting technologies and rolling capacity and the mastery of heat treatment properties of materials, the physical quality level of the extra-thick steel plates for the pressure vessels has been greatly improved, and pressure vessel manufacturers have accumulated richer experience in the manufacture of large-thickness plate-welded vessels, and especially find out a set of feasible mature process in the aspect of thick-walled tube section forming. With the progress of extra-thick steel plate manufacturing technologies and plate welding forming technologies, the upsizing of the plate-welded pressure vessels has achieved a great development. At present, the maximum wall thickness of the plate-welded pressure vessels has reached 200 mm, the pressure vessels with a wall thickness greater than 200 mm completely have the plate welding forming capacity, and the technical bottleneck of the pressure vessels is that the physical quality level and stability of extra-thick steel plates for the pressure vessels have not yet been broken through, which is not enough to fully meet the current manufacturing requirements of the thick-walled vessels, especially the extra-thick steel plates for the pressure vessels serving in a wet hydrogen sulfide low temperature corrosive environment, so that not only good internal quality, good welding performance and well-matched mechanical properties are required, but also excellent hydrogen-induced cracking resistance should be possessed to ensure safety of efficient operation of equipment, and the production difficulty is extremely large.
Therefore, it is imperative and imminent to replace the forgings with thick steel plates. With the improvement of smelting technologies and rolling capacity and the mastery of heat treatment properties of materials, the physical quality level of the extra-thick steel plates for the pressure vessels has been greatly improved, and pressure vessel manufacturers have accumulated richer experience in the manufacture of large-thickness plate-welded vessels, and especially find out a set of feasible mature process in the aspect of thick-walled tube section forming. With the progress of extra-thick steel plate manufacturing technologies and plate welding forming technologies, the upsizing of the plate-welded pressure vessels has achieved a great development. At present, the maximum wall thickness of the plate-welded pressure vessels has reached 200 mm, the pressure vessels with a wall thickness greater than 200 mm completely have the plate welding forming capacity, and the technical bottleneck of the pressure vessels is that the physical quality level and stability of extra-thick steel plates for the pressure vessels have not yet been broken through, which is not enough to fully meet the current manufacturing requirements of the thick-walled vessels, especially the extra-thick steel plates for the pressure vessels serving in a wet hydrogen sulfide low temperature corrosive environment, so that not only good internal quality, good welding performance and well-matched mechanical properties are required, but also excellent hydrogen-induced cracking resistance should be possessed to ensure safety of efficient operation of equipment, and the production difficulty is extremely large.
[04] At present, the domestic hydrogen-induced cracking-resistant steel plate SA516Gr70 (HIC) reported publicly in China has a maximum thickness of 200 mm, and hydrogen-induced cracking-resistant steel plates with a thickness greater than 200 mm for pressure vessels still rely on imports. There are few patents related to large-thickness hydrogen-induced cracking-resistant steel used in the wet hydrogen sulfide environment for pressure vessels. The publication number CN10108330398A relates to "a method for producing an extra-thick acid-resistant plate for vessels", and provides a hydrogen-induced cracking-resistant steel plate for pressure vessels, which is produced by steel ingots.
Reasonable properties are obtained through Cr, Ni and Cu multi-alloying design and subsequent normalizing heat treatment. However, the maximum thickness of the steel plate is only 200 mm, and in the performance description, the impact temperature is only -20 C, flaw detection meets requirements of Level I, but the flaw detection standard is not specified, and the application range is small. The publication number CN111349859A relates to "a steel plate with large thickness, 500 Mpa grade and high Z-direction layered performance for low-temperature vessel and rolled by compound blank and a method for manufacturing the same", and provides an extra-thick steel plate for low-temperature vessels, which is produced by the compound blank, and a blank compounding manner is to compound two blanks.
Reasonable properties are obtained through Nb and V microalloy combination design and subsequent normalizing heat treatment. However, the maximum thickness of the steel plate is 210 mm, and in the performance description, the flaw detection meets Level I
of the NB/T47013.3 standard, but hydrogen-induced cracking resistance is not mentioned. The publication number CN109355579A relates to "an extra-thick steel plate 12Cr2Mo1VR for high-temperature pressure vessels and a method for manufacturing the same", and provides an extra-thick steel plate for high-temperature pressure vessels, which is produced by water-cooled die-casting steel ingots. Reasonable properties are obtained through reasonable composition design and subsequent two times of quenching + two times of tempering heat treatment. In addition, the maximum thickness of the steel plate is 300 mm, and in the performance description, the internal quality of the steel plate is poor, and the flaw detection can only meet Level III of the J B/T47013 standard. However, the hydrogen-induced cracking resistance is not mentioned, requirements of replacing the forgings cannot be met, and the steel plate is not suitable for use in the wet hydrogen sulfide corrosive environment. The publication number CN108754321B relates to "an extra-thick normalized high-strength steel plate for a pressure vessel and a method for manufacturing the same", and provides an extra-thick normalized high-strength steel plate for a pressure vessel, which is produced by a compound blank, and .a blank compounding manner is to compound three blanks Reasonable performance is obtained through Ni and Cu alloy composition design and subsequent normalizing heat treatment, the maximum thickness of the steel plate is 250 mm, and in the performance description, the impact temperature is only 0 C, and the flaw detection can only meet Level I of the J B/1-47013 standard. The hydrogen-induced cracking resistance is not mentioned, and the steel plate is not suitable for use in the wet hydrogen sulfide low-temperature corrosive environment.
SUMMARY OF THE INVENTION
Reasonable properties are obtained through Cr, Ni and Cu multi-alloying design and subsequent normalizing heat treatment. However, the maximum thickness of the steel plate is only 200 mm, and in the performance description, the impact temperature is only -20 C, flaw detection meets requirements of Level I, but the flaw detection standard is not specified, and the application range is small. The publication number CN111349859A relates to "a steel plate with large thickness, 500 Mpa grade and high Z-direction layered performance for low-temperature vessel and rolled by compound blank and a method for manufacturing the same", and provides an extra-thick steel plate for low-temperature vessels, which is produced by the compound blank, and a blank compounding manner is to compound two blanks.
Reasonable properties are obtained through Nb and V microalloy combination design and subsequent normalizing heat treatment. However, the maximum thickness of the steel plate is 210 mm, and in the performance description, the flaw detection meets Level I
of the NB/T47013.3 standard, but hydrogen-induced cracking resistance is not mentioned. The publication number CN109355579A relates to "an extra-thick steel plate 12Cr2Mo1VR for high-temperature pressure vessels and a method for manufacturing the same", and provides an extra-thick steel plate for high-temperature pressure vessels, which is produced by water-cooled die-casting steel ingots. Reasonable properties are obtained through reasonable composition design and subsequent two times of quenching + two times of tempering heat treatment. In addition, the maximum thickness of the steel plate is 300 mm, and in the performance description, the internal quality of the steel plate is poor, and the flaw detection can only meet Level III of the J B/T47013 standard. However, the hydrogen-induced cracking resistance is not mentioned, requirements of replacing the forgings cannot be met, and the steel plate is not suitable for use in the wet hydrogen sulfide corrosive environment. The publication number CN108754321B relates to "an extra-thick normalized high-strength steel plate for a pressure vessel and a method for manufacturing the same", and provides an extra-thick normalized high-strength steel plate for a pressure vessel, which is produced by a compound blank, and .a blank compounding manner is to compound three blanks Reasonable performance is obtained through Ni and Cu alloy composition design and subsequent normalizing heat treatment, the maximum thickness of the steel plate is 250 mm, and in the performance description, the impact temperature is only 0 C, and the flaw detection can only meet Level I of the J B/1-47013 standard. The hydrogen-induced cracking resistance is not mentioned, and the steel plate is not suitable for use in the wet hydrogen sulfide low-temperature corrosive environment.
SUMMARY OF THE INVENTION
[05] The technical problem to be solved by the present invention is to provide hydrogen-induced cracking-resistant steel for a pressure vessel and a method for manufacturing the same in view of the above-mentioned prior arts. A thickness of a steel plate is > 200-250 mm, and the steel plate still has well-matched mechanical properties and excellent hydrogen-induced cracking resistance after high-temperature long-time simulated post-weld heat treatment, is suitable for use in a wet hydrogen sulfide environment, and fully meets requirements of a plate welding manufacturing process for thick-walled pressure vessels.
[06] The technical solution adopted by the present invention to solve the above-mentioned problems is: a hydrogen-induced cracking-resistant steel plate with a thickness > 200-250 mm for a pressure vessel. The steel plate has a chemical composition designed to include, by weight percentage: C: 0.10-0.20%, Si: 0.15-0.40%, Mn:
0.95-1.35%, P:
0.005%, S: 5 0.0008%, Cr: 0.10-0.30%, Ni: 0.25-0.40%, Mo: 0.08-0.12%, Alt:
0.02-0.05%, Nb:
0.01-0.02%, V: 0.01-0.03%, Ti: 0.01-0.02%, B: 5 0.0005%, and the balance being Fe and inevitable impurity elements. At the same time, the chemical composition has a carbon equivalent Ceq 5 0.45%, wherein Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15.
0.95-1.35%, P:
0.005%, S: 5 0.0008%, Cr: 0.10-0.30%, Ni: 0.25-0.40%, Mo: 0.08-0.12%, Alt:
0.02-0.05%, Nb:
0.01-0.02%, V: 0.01-0.03%, Ti: 0.01-0.02%, B: 5 0.0005%, and the balance being Fe and inevitable impurity elements. At the same time, the chemical composition has a carbon equivalent Ceq 5 0.45%, wherein Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15.
[07] The present invention relates to the steel plate with well-matched comprehensive mechanical properties and excellent hydrogen-induced cracking resistance for the pressure vessel, and belongs to an iron-based alloy. Main chemical elements in steel and their functions are as follows:
[08] C can significantly improve the strength of the steel plate, but as a carbon content increases, the toughness of the steel plate decreases, and carbide segregation is prone to occurrence, causing differences in the hardness of a segregation zone and surrounding tissues, and resulting in hydrogen-induced crack corrosion. Comprehensively considering the strength, toughness and hydrogen-induced cracking resistance of the steel plate, the C
content in the present invention is set at 0.10-0.20%.
content in the present invention is set at 0.10-0.20%.
[09] Mn improves the strength of the steel through solid solution strengthening, but when Mn is added to more than 1.05%, the sensitivity to hydrogen-induced cracking increases, so a Mn content should not be too high. Comprehensively considering the strength and hydrogen-induced cracking resistance of the steel plate, the Mn content in the present invention is set at 0.95-1.35%.
[010] Si is mainly used as a reducing agent and a deoxidizer during steelmaking and has a certain solid solution strengthening effect. At the same time, an Si element is easy to segregate to grain boundaries, which promotes the generation of intergranular cracks. In addition, when a Si content is slightly higher, the hardness of a welding seam and a heat affected zone cannot be controlled, so the Si content in the present invention is set at 0.15-0.40%.
[011] Cr is an element that improves hardenability and can significantly increase the strength of the steel, but if a content is too high, a brittle transition temperature will be increased.
A control range of the Cr content in the present application is 0.10-0.30%.
A control range of the Cr content in the present application is 0.10-0.30%.
[012] Ni mainly plays a role in solid solution strengthening in the steel and can improve the toughness at the same time, but a too high Ni content will significantly increase the cost, so its use should be restricted. A control range of the Ni content in the present application is 0.25-0.40%.
[013] Mo is an element that improves hardenability and can significantly increase the strength of the steel. A control range of a Mo content in the present application is 0.08-0.12%.
[014] Alt is mainly used for deoxidation and grain refinement, and an Al content in the present patent is controlled at 0.02-0.05%.
[015] Nb can significantly increase an austenite recrystallization temperature of the steel, expand a range of a recrystallization zone, and facilitate achievement of high-temperature rolling. Nb can also inhibit the growth of austenite grains, and has the effects of fine grain strengthening and precipitation strengthening. A Nb content in the present patent is controlled at 0.01-0.02%.
[016] V and Ti form carbonitrides with C and N elements, have the effects of delaying austenite recrystallization and refining ferrite grains, and can simultaneously improve the strength and toughness of the steel plate. A V content in the present patent is controlled at 0.010-0.03%, and a Ti content is controlled at 0.010-0.02%.
[017] P and S are harmful elements. With the increase of an S content in the steel, contents of MnS and FeS also increase, resulting in local microstructure loosening and increasing the sensitivity to hydrogen-induced cracking. When a P content is very low, cracks can nucleate on MnS, but the size is too small to be detected. However, if the P content is high (for example, P=0.4%), even if the S content is very low (S=0.001%), the cracks can also nucleate and propagate on oxide inclusions and grain boundaries. Therefore, in the present invention, the S content is set to be 5 0.0008%, and the P content is set to be 5 0.005%.
[018] The steel plate product of the present invention is produced by a compound blank, and the main process steps are successively continuous casting blank smelting and casting, vacuum welding combined blank making, compound blank cogging and rolling, finished steel plate rolling, and heat treatment. The specific operations are as follows:
[019] (1) Continuous casting blank smelting and casting
[020] 450 mm section continuous casting blanks with the same size produced by a same smelting furnace number are taken as blanks of the compound blank, the continuous casting blanks adopt a pure steel smelting process, measures such as large tundish casting and prolonging of the soft argon gas blowing time are taken to make non-metallic inclusions fully float to slag, so that a content of the non-metallic inclusions in the steel is reduced, the purity of molten steel is improved, and the non-metallic inclusions of Class A, Class B, Class C and Class D in the molten steel are controlled to be 5 1.0 grade in individual item and 5 2.5 grade in sum; through a low superheat argon protection casting process and a dynamic soft reduction technology, segregation of the continuous casting blanks is controlled to be below 1.0 grade for Class C and porosity is controlled to be below 0.5 grade; and after discharged from a production line, the continuous casting blanks are added with a cover to be slowly cooled for 72 h to fully diffuse hydrogen.
[021] Further, production technology processes of the continuous casting blanks are: KR
pretreatment ¨> converter smelting ¨> LF refining ¨> RH refining ¨> continuous casting. The converter smelting is followed by slag-off treatment, the soft argon gas blowing time is longer than 30 min after RH breakout, and a molten steel casting superheat temperature in a continuous casting process is 10-30 C.
pretreatment ¨> converter smelting ¨> LF refining ¨> RH refining ¨> continuous casting. The converter smelting is followed by slag-off treatment, the soft argon gas blowing time is longer than 30 min after RH breakout, and a molten steel casting superheat temperature in a continuous casting process is 10-30 C.
[022] (2) Vacuum welding combined blank making: after surfaces of the continuous casting blanks are milled and ground, electron beam welding and combination are carried out in a vacuum chamber, a blank compounding manner is to compound two blanks, the compound blank is made by using a disclosed conventional process, and a thickness of the obtained compound blank is 860-870 mm.
[023] (3) Compound blank cogging and rolling: the compound blank is heated by a soaking furnace, and while the segregation of the blanks is fully diffused, partial metallurgical bonding of compound interfaces is completed through high-temperature diffusion; and a single-stand high-permeability rolling process is adopted in a roughing mill, rolling passes are reasonably allocated, repeated recrystallization is carried out to enable the compound interfaces to achieve firm metallurgical bonding, a thickness of an intermediate blank is controlled at 400-450 mm, and after rolled and discharged from the production line, the blank enters the cover to be slowly cooled for 72 h to fully diffuse hydrogen.
[024] Further, the compound blank adopts a sectional heating process: the steel is charged below 550 C, and the steel is sealed for 1-2 hours; in a low temperature section, the temperature rises to 820 20 C at a speed of not more than 75 C/h, and is kept for 3-5 hours;
in a medium temperature section, the temperature rises to 1000 20 C at a speed of not more than 110 C/h, and is kept for 2 hours; and in a high temperature section, a temperature rise speed is not limited, and the temperature rises to 1220-1250 C, and is kept for 8-12 hours.
in a medium temperature section, the temperature rises to 1000 20 C at a speed of not more than 110 C/h, and is kept for 2 hours; and in a high temperature section, a temperature rise speed is not limited, and the temperature rises to 1220-1250 C, and is kept for 8-12 hours.
[025] Further, a main task of a compound blank cogging process is to complete rolling and compounding on the roughing mill to obtain the intermediate blank with a reasonable size, an initial rolling temperature is 1060-1100 C, a finish rolling temperature is 950-980 C, a high-permeability rolling process is adopted, and a single-pass rolling reduction of at least 4 rolling passes in longitudinal rolling passes is 50 mm. After discharged from the production line, the steel plate is added with a cover to be slowly cooled for 72 hours.
[026] (4) Finished steel plate rolling: after the intermediate blank is slowly cooled and finished, heating is carried out again in a walking heating furnace to make the intermediate blank completely austenitized, segregation defects in a core of the blank is further reduced through second-time high-temperature diffusion heating, and at the same time, convenience is provided for achieving second-time high-permeability rolling. Further, the intermediate blank adopts a sectional heating manner: the total heating time is 620 min, the temperature of a second heating section is 1200-1250 C, the temperature of a soaking section is 1180-1250 C, and the total heating time of the second heating section and the soaking section is 270 min to ensure that segregation of the casting blanks is fully diffused.
[027] Rolling is divided into two stages: rough rolling and finish rolling;
rolling deformation is mainly concentrated in the rough rolling stage, a high-permeability rolling process is adopted in the stage, and a single-pass rolling reduction of at least 2 rolling passes is 50 mm; and a main task of finish rolling is to accurately control a thickness tolerance and obtain a good plate shape, an initial rolling temperature of the finish rolling is 820 20 C, and a stand-up thickness is a thickness of the finished steel plate + 30 mm. In other words, total rolling deformation in the thickness direction of the steel plate in the finish rolling stage is 30 mm;
and after discharged from the production line, the steel plate is stacked to be slowly cooled for 48 hours to fully diffuse hydrogen.
rolling deformation is mainly concentrated in the rough rolling stage, a high-permeability rolling process is adopted in the stage, and a single-pass rolling reduction of at least 2 rolling passes is 50 mm; and a main task of finish rolling is to accurately control a thickness tolerance and obtain a good plate shape, an initial rolling temperature of the finish rolling is 820 20 C, and a stand-up thickness is a thickness of the finished steel plate + 30 mm. In other words, total rolling deformation in the thickness direction of the steel plate in the finish rolling stage is 30 mm;
and after discharged from the production line, the steel plate is stacked to be slowly cooled for 48 hours to fully diffuse hydrogen.
[028] (5) Heat treatment: the steel plate is normalized and tempered in turn, and water accelerated cooling is adopted in a water tank after normalizing.
[029] Further, a normalizing heating temperature is 880-910 C, a temperature keeping time coefficient is 2.0-2.5 min/mm, and the steel plate is taken out of a furnace and cooled by water, so that a surface of the steel plate is cooled to 400-500 C; and in order to prevent the strength of the steel plate after the simulated post-weld heat treatment from being greatly reduced, a tempering temperature of the steel plate is not lower than that of the simulated post-weld heat treatment, and for tempering, a tempering temperature is 610-630 C, and the temperature keeping time coefficient is 3.5-4.5 min/mm.
[030] The main technical difficulties of large-thickness hydrogen-induced cracking-resistant steel plates for pressure vessels, especially products that replace the forgings, are mainly reflected in: the internal quality, hydrogen-induced cracking resistance and core mechanical properties of the steel plates are difficult to guarantee due to limitations of the metallurgical quality of blanks themselves and the capacity of rolling mills.
In order to solve the problems, the present invention has taken corresponding technological measures in the aspect of a method for manufacturing the product, specifically as follows:
In order to solve the problems, the present invention has taken corresponding technological measures in the aspect of a method for manufacturing the product, specifically as follows:
[031] (1) the compound blank is adopted to replace steel ingots, and the blank compounding manner is to compound two blanks;
[032] (2) by reducing the contents of easily segregated elements such as C, Mn, S and P, reducing the continuous casting molten steel superheat temperature and adopting dynamic soft reduction, metallurgical defects of the segregation and porosity of the continuous casting blanks are reduced, the segregation of the casting blanks is controlled to be below 1.0 grade for Class C, the porosity defect is controlled to be below 0.5 grade, and the range of the continuous casting molten steel superheat temperature in the present invention is 10-30 C;
[033] (3) by taking the measures such as large tundish casting and prolonging of the soft argon gas blowing time, the non-metallic inclusions can fully float to the slag, so that the content of the non-metallic inclusions in the steel is reduced, the purity of molten steel is improved, and the non-metallic inclusions of Class A, Class B, Class C and Class D in the molten steel are controlled to be 5 1.0 grade in individual item and 5 2.5 grade in sum; and the soft argon gas blowing time in the present invention is controlled to be longer than 30 min;
[034] (4) a two-heat steel rolling process of first cogging and then rolling is adopted;
and through two times of high-temperature diffusion heating and the high-permeability rolling process, the segregation is fully diffused, and the porosity defect is pressed; and
and through two times of high-temperature diffusion heating and the high-permeability rolling process, the segregation is fully diffused, and the porosity defect is pressed; and
[035] (5) a normalizing + water accelerated cooling + tempering heat treatment process is adopted; and through microstructure regulation, a metallographic structure is more uniform and finer, and the core mechanical properties and hydrogen-induced cracking resistance are improved.
[036] The principle of the present invention to adopt the above mentioned process measures and the range of applicability of process parameters is as follows:
[037] Since the continuous casting blank cools faster during a solidification process, its internal quality is significantly better than that of traditional steel ingots. The present invention adopts the compound blanks as the blanks, which not only solves the insufficient compression ratio for production of single blanks of the continuous casting blanks, but also solves the practical problems of serious metallurgical defects of segregation and porosity at the core of the steel ingot The purpose of adopting the blank compounding manner of compounding two blanks is to make the core of the steel plate avoid the metallurgical defects at thickness 1/2 positions of the continuous casting blanks, so as to improve the core performance of the steel plate.
Compared with a single blank production manner of the continuous casting blanks, its disadvantage is that upper and lower 1/4 positions in the thickness direction of the two-slab compound steel plate are exactly the thickness 1/2 positions of the continuous casting blanks and are also positions where the metallurgical defects of the segregation and porosity are concentrated, the number is changed from one to two, but positions of the metallurgical defects of the segregation and porosity distributed in the thickness direction are relatively moved outward and closer to upper and lower surfaces of the compound blank, which is conducive to the high-temperature heating and diffusion of the segregation and the high-permeability rolling and pressing of the porosity defects. Since the metallurgical defects such as the segregation and porosity cannot be avoided, in the present invention, through measures of reducing the contents of the easily segregated elements such as C, Mn, S and P, reducing the continuous casting molten steel superheat temperature, adopting the dynamic soft rolling reduction and the like, the segregation of the casting blanks is controlled to be below 1.0 grade for Class C, the porosity defects are controlled to be below 0.5 grade, so as to ensure the metallurgical quality, mechanical properties and hydrogen-induced cracking resistance of the upper and lower thickness 1/4 positions of the steel plate.
Compared with a single blank production manner of the continuous casting blanks, its disadvantage is that upper and lower 1/4 positions in the thickness direction of the two-slab compound steel plate are exactly the thickness 1/2 positions of the continuous casting blanks and are also positions where the metallurgical defects of the segregation and porosity are concentrated, the number is changed from one to two, but positions of the metallurgical defects of the segregation and porosity distributed in the thickness direction are relatively moved outward and closer to upper and lower surfaces of the compound blank, which is conducive to the high-temperature heating and diffusion of the segregation and the high-permeability rolling and pressing of the porosity defects. Since the metallurgical defects such as the segregation and porosity cannot be avoided, in the present invention, through measures of reducing the contents of the easily segregated elements such as C, Mn, S and P, reducing the continuous casting molten steel superheat temperature, adopting the dynamic soft rolling reduction and the like, the segregation of the casting blanks is controlled to be below 1.0 grade for Class C, the porosity defects are controlled to be below 0.5 grade, so as to ensure the metallurgical quality, mechanical properties and hydrogen-induced cracking resistance of the upper and lower thickness 1/4 positions of the steel plate.
[038] The non-metallic inclusions are hydrogen traps. When hydrogen enters the steel, hydrogen molecules will be formed by enriching at inclusion interfaces. When a hydrogen pressure exceeds the strength limit of materials, hydrogen-induced cracking will be formed at positions with inhomogeneous structures. According to the present invention, the measures such as large tundish casting and prolonging of the soft argon gas blowing time are taken, so that the non-metallic inclusions can fully float to the slag, and the non-metallic inclusions of Class A, Class B, Class C and Class D in the molten steel of the continuous casting blanks are controlled to be 5 1.0 grade in individual item and 5 2.5 grade in sum. By controlling the content, size and shape of the non-metallic inclusions, the sensitivity to hydrogen-induced cracking of the steel plate for the pressure vessel can be reduced, thereby improving the hydrogen-induced cracking resistance.
[039] Limited by the capacity of the rolling mill, it is difficult for a rolling force to penetrate into the core of the steel plate during the rolling process. The conventional rolling process cannot guarantee the internal quality and core performance of the steel plate.
At the same time, due to the large thickness of the steel plate, the grain refining effect is not obvious through a controlled rolling and controlled cooling process, even under normalizing process conditions, due to a low cooling rate in air, grains of the steel plate will still be relatively coarse, and the strength, low-temperature impact toughness, hydrogen-induced cracking resistance and stability of the steel plate are difficult to meet the design requirements. In order to make extra-thick steel plates have the quality and performance of the forgings with a same thickness, and fully meet the manufacturing process requirements of plate welding instead of forge welding, the present invention adopts the two-heat steel rolling process of first cogging and rolling; through two times of high-temperature diffusion heating and the high-permeability rolling process, the segregation is fully diffused, and the porosity defects are pressed; and in terms of heat treatment, through microstructure regulation, the normalizing + water accelerated cooling + tempering process is adopted to make the metallographic structure more uniform and finer, which greatly improves various properties of the steel plate, especially the low-temperature impact toughness and hydrogen-induced cracking resistance of the core.
At the same time, due to the large thickness of the steel plate, the grain refining effect is not obvious through a controlled rolling and controlled cooling process, even under normalizing process conditions, due to a low cooling rate in air, grains of the steel plate will still be relatively coarse, and the strength, low-temperature impact toughness, hydrogen-induced cracking resistance and stability of the steel plate are difficult to meet the design requirements. In order to make extra-thick steel plates have the quality and performance of the forgings with a same thickness, and fully meet the manufacturing process requirements of plate welding instead of forge welding, the present invention adopts the two-heat steel rolling process of first cogging and rolling; through two times of high-temperature diffusion heating and the high-permeability rolling process, the segregation is fully diffused, and the porosity defects are pressed; and in terms of heat treatment, through microstructure regulation, the normalizing + water accelerated cooling + tempering process is adopted to make the metallographic structure more uniform and finer, which greatly improves various properties of the steel plate, especially the low-temperature impact toughness and hydrogen-induced cracking resistance of the core.
[040] Compared with the prior art, the present invention has the advantages that:
[041] The present invention belongs to the large-thickness hydrogen-induced cracking-resistant steel plate for the pressure vessel. The steel plate has the thickness of >
200-250 mm. The steel plate has the well-matched comprehensive mechanical properties and excellent hydrogen-induced cracking resistance. The strength and low temperature impact toughness of the steel plate are not significantly weakened after the high-temperature long-time simulated post-weld heat treatment. The steel plate is tested for hydrogen-induced cracking resistance according to an A solution in NACE TM0284-2016 "Experimental Method for Property Evaluation of Hydrogen-induced Cracking-Resistant Steel for Pipeline Pressure Vessel". The crack length ratio (CLR), crack width ratio (CTR) and crack sensitivity rate (CSR) of single test sections is 0. There is no hydrogen bubbling, that is, there is no defect after corrosion. After 610 10 C x 30 h simulated post-weld heat treatment, the mechanical properties are tested, which can meet the yield strength 320 Mpa, tensile strength 520 Mpa, core -30 C transverse Charpy impact energy single value 100J, Z tensile section shrinkage 35% and steel plate surface Brinell hardness 5 180 HB.
BRIEF DESCRIPTION OF THE DRAWINGS
200-250 mm. The steel plate has the well-matched comprehensive mechanical properties and excellent hydrogen-induced cracking resistance. The strength and low temperature impact toughness of the steel plate are not significantly weakened after the high-temperature long-time simulated post-weld heat treatment. The steel plate is tested for hydrogen-induced cracking resistance according to an A solution in NACE TM0284-2016 "Experimental Method for Property Evaluation of Hydrogen-induced Cracking-Resistant Steel for Pipeline Pressure Vessel". The crack length ratio (CLR), crack width ratio (CTR) and crack sensitivity rate (CSR) of single test sections is 0. There is no hydrogen bubbling, that is, there is no defect after corrosion. After 610 10 C x 30 h simulated post-weld heat treatment, the mechanical properties are tested, which can meet the yield strength 320 Mpa, tensile strength 520 Mpa, core -30 C transverse Charpy impact energy single value 100J, Z tensile section shrinkage 35% and steel plate surface Brinell hardness 5 180 HB.
BRIEF DESCRIPTION OF THE DRAWINGS
[042] Fig. 1 is a diagram of a metallographic structure of a steel plate with a thickness of 250 mm in Embodiment 3 of the present invention (thickness 1/4 position).
[043] Fig. 2 is a diagram of a metallographic structure of a steel plate with a thickness of 250 mm in Embodiment 3 of the present invention (thickness 1/2 position).
[044] Fig. 3 is a diagram of a metallographic structure of a steel plate with a thickness of 250 mm in Embodiment 3 of the present invention (thickness 3/4 position).
DETAILED DESCRIPTION OF EMBODIMENTS
DETAILED DESCRIPTION OF EMBODIMENTS
[045] The present invention will be further described in detail below in conjunction with embodiments and comparative examples.
[046] Embodiment 1
[047] A thickness of a hydrogen-induced cracking-resistant steel plate for a pressure vessel in the embodiment is 210 mm, and chemical compositions of the hydrogen-induced cracking-resistant steel plate for the pressure vessel include, by weight percentage: C: 0.15%, Si: 0.28%, Mn: 1.23%, P: 0.004%, S: 5 0.0006%, Cr: 0.20%, Ni: 0.32%, Mo:
0.10%, Alt: 0.032%, Nb: 0.015%, V: 0.015%, Ti: 0.015%, and the rest being Fe and inevitable impurity elements, a carbon equivalent Ceq 5 0.45%, and Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15.
0.10%, Alt: 0.032%, Nb: 0.015%, V: 0.015%, Ti: 0.015%, and the rest being Fe and inevitable impurity elements, a carbon equivalent Ceq 5 0.45%, and Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15.
[048] A manufacturing process of the steel plate is as follows:
[049] The steel plate product of the present invention is produced by a compound blank, and the main process steps are successively continuous casting blank smelting and casting, vacuum welding combined blank making, compound blank cogging and rolling, finished steel plate rolling, and heat treatment. The specific operations are as follows:
[050] (1) Continuous casting blank smelting and casting
[051] 450 mm section continuous casting blanks with the same size produced by a same smelting furnace number are taken as blanks of a compound blank, the continuous casting blanks adopt a pure steel smelting process, measures such as large tundish casting and prolonging of the soft argon gas blowing time are taken to make non-metallic inclusions fully float to slag, so that a content of the non-metallic inclusions in steel is reduced, the purity of molten steel is improved, and the non-metallic inclusions of Class A, Class B, Class C and Class D in the molten steel are controlled to be 5 1.0 grade in individual item and 5 2.5 grade in sum; through a low superheat argon protection casting process and a dynamic soft reduction technology, segregation of the continuous casting blanks is controlled to be below 1.0 grade for Class C and porosity is controlled to be below 0.5 grade; and after discharged from a production line, the continuous casting blanks are added with a cover to be slowly cooled for 72 h to fully diffuse hydrogen.
[052] Further, production technology processes of the continuous casting blanks are: KR
pretreatment ¨> converter smelting ¨> LF refining ¨> RH refining ¨> continuous casting. The converter smelting is followed by slag-off treatment, the soft argon gas blowing time is 35 min after RH breakout, and the molten steel casting superheat temperature in a continuous casting process is 22 C.
pretreatment ¨> converter smelting ¨> LF refining ¨> RH refining ¨> continuous casting. The converter smelting is followed by slag-off treatment, the soft argon gas blowing time is 35 min after RH breakout, and the molten steel casting superheat temperature in a continuous casting process is 22 C.
[053] (2) Vacuum welding combined blank making: after surfaces of the continuous casting blanks are milled and ground, electron beam welding and combination are carried out in a vacuum chamber, a blank compounding manner is to compound two blanks, the compound blank is made by using a disclosed conventional process, and a thickness of the obtained compound blank is 865 mm.
[054] (3) Compound blank cogging and rolling: the compound blank is heated by a soaking furnace, and while the segregation of the blanks is fully diffused, partial metallurgical bonding of compound interfaces is completed through high-temperature diffusion; and a single-stand high-permeability rolling process is adopted in a roughing mill, rolling passes are reasonably allocated, repeated recrystallization is carried out to enable the compound interfaces to achieve firm metallurgical bonding, a thickness of an intermediate blank is 425 mm, and after rolled and discharged from the production line, the blank enters the cover to be slowly cooled for 72 h to fully diffuse hydrogen.
[055] Further speaking, the compound blank adopts a sectional heating process:
the steel is charged below 540 C, and the steel is sealed for 2 hours; in a low temperature section, the temperature rises to 835 C at a speed of 70 C/h, and is kept for 4 hours;
in a medium temperature section, the temperature rises to 1010 C at a speed of 100 C/h, and is kept for 2 hours; and in a high temperature section, a temperature rise speed is not limited, and the temperature rises to 1245 C, and is kept for 11 hours.
the steel is charged below 540 C, and the steel is sealed for 2 hours; in a low temperature section, the temperature rises to 835 C at a speed of 70 C/h, and is kept for 4 hours;
in a medium temperature section, the temperature rises to 1010 C at a speed of 100 C/h, and is kept for 2 hours; and in a high temperature section, a temperature rise speed is not limited, and the temperature rises to 1245 C, and is kept for 11 hours.
[056] Further, a main task of a compound blank cogging process is to complete rolling and compounding on the roughing mill to obtain the intermediate blank with a reasonable size, an initial rolling temperature is 1080 C, a finish rolling temperature is 970 C, a high-permeability rolling process is adopted, a single-pass rolling reduction of 4 rolling passes in longitudinal rolling passes is 50 mm, being 55 mm, 55 mm, 52 mm and 52 mm respectively.
[057] After discharged from the production line, the steel plate is added with a cover to be slowly cooled for 72 hours.
[058] (4) Finished steel plate rolling: after the intermediate blank is slowly cooled and finished, heating is carried out again in a walking heating furnace to make the intermediate blank completely austenitized, segregation defects in a core of the blank is further reduced through second-time high-temperature diffusion heating, and at the same time, convenience is provided for achieving second-time high-permeability rolling. Further, the intermediate blank adopts a sectional heating manner: the total heating time is 620 min, the temperature of a second heating section is 1200-1250 C, the temperature of a soaking section is 1180-1250 C, and the total heating time of the second heating section and the soaking section is 300 min to ensure that the segregation of the casting blanks is fully diffused.
[059] Rolling is divided into two stages: rough rolling and finish rolling;
rolling deformation is mainly concentrated in the rough rolling stage, the high-permeability rolling process is adopted in the stage, a single-pass rolling reduction of 2 rolling passes is 50 mm, being 56 mm and 52 mm respectively; a main task of the finish rolling is to accurately control a thickness tolerance and obtain a good plate shape; an initial rolling temperature of finish rolling is 820 C, and a stand-by thickness is 240 mm; and after discharged from the production line, the steel plate is stacked to be slowly cooled for 48 hours to fully diffuse hydrogen.
rolling deformation is mainly concentrated in the rough rolling stage, the high-permeability rolling process is adopted in the stage, a single-pass rolling reduction of 2 rolling passes is 50 mm, being 56 mm and 52 mm respectively; a main task of the finish rolling is to accurately control a thickness tolerance and obtain a good plate shape; an initial rolling temperature of finish rolling is 820 C, and a stand-by thickness is 240 mm; and after discharged from the production line, the steel plate is stacked to be slowly cooled for 48 hours to fully diffuse hydrogen.
[060] (5) Heat treatment: the steel plate is normalized and tempered in turn, and water accelerated cooling is adopted in a water tank after normalizing.
[061] Further, a normalizing heating temperature is 900 C, a temperature keeping time coefficient is 2.0 min/mm, and the steel plate is taken out of a furnace and cooled by water, so that the surface of the steel plate is cooled to 450 C; in order to prevent the strength of the steel plate from being greatly reduced, a tempering temperature of the steel plate is not lower than that of the simulated post-weld heat treatment; and for tempering, a tempering temperature is 630 C, and the temperature keeping time coefficient is 3.5 min/mm.
[062] The hydrogen-induced cracking-resistant steel plate with the thickness of 210 mm for the pressure vessel, produced by the above-mentioned manufacturing process, has well-matched mechanical properties and excellent hydrogen-induced cracking resistance. The mechanical properties of the steel plate are shown in Table 1 in detail, and the hydrogen-induced cracking resistance is shown in Table 2. The flaw detection of the steel plate meets requirements of Level TI of the NB/T47013.3 standard.
[063] Embodiment 2
[064] A thickness of a hydrogen-induced cracking-resistant steel plate for a pressure vessel in the embodiment is 230mm, and chemical compositions of the hydrogen-induced cracking-resistant steel plate for the pressure vessel include, by weight percentage: C: 0.14%, Si: 0.27%, Mn: 1.26%, P: 0.003%, 5: 5 0.0004%, Cr: 0.21%, Ni: 0.35%, Mo:
0.10%, Alt: 0.030%, Nb: 0.016%, V: 0.020%, Ti: 0.017%, and the rest being Fe and inevitable impurity elements, a carbon equivalent Ceq 5 0.45%, and Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15.
0.10%, Alt: 0.030%, Nb: 0.016%, V: 0.020%, Ti: 0.017%, and the rest being Fe and inevitable impurity elements, a carbon equivalent Ceq 5 0.45%, and Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15.
[065] A manufacturing process of the steel plate is as follows:
[066] The steel plate product of the present invention is produced by a compound blank, and the main process steps are successively continuous casting blank smelting and casting, vacuum welding combined blank making, compound blank cogging and rolling, finished steel plate rolling, and heat treatment. The specific operations are as follows:
[067] (1) Continuous casting blank smelting and casting
[068] 450 mm section continuous casting blanks with the same size produced by a same smelting furnace number are taken as blanks of a compound blank, the continuous casting blanks adopt a pure steel smelting process, measures such as large tundish casting and prolonging of the soft argon gas blowing time are taken to make non-metallic inclusions fully float to slag, so that a content of the non-metallic inclusions in steel is reduced, the purity of molten steel is improved, and the non-metallic inclusions of Class A, Class B, Class C and Class D in the molten steel are controlled to be 5 1.0 grade in individual item and 5 2.5 grade in sum; through a low superheat argon protection casting process and a dynamic soft reduction technology, segregation of the continuous casting blanks is controlled to be below 1.0 grade for Class C and porosity is controlled to be below 0.5 grade; and after discharged from a production line, the continuous casting blanks are added with a cover to be slowly cooled for 72 h to fully diffuse hydrogen.
[069] Further, production technology processes of the continuous casting blanks are: KR
pretreatment¨converter smelting¨>LF refining¨>RH refining¨continuous casting.
The converter smelting is followed by slag-off treatment, the soft argon gas blowing time is 32min after RH breakout, and the molten steel casting superheat temperature in a continuous casting process is 20 C.
pretreatment¨converter smelting¨>LF refining¨>RH refining¨continuous casting.
The converter smelting is followed by slag-off treatment, the soft argon gas blowing time is 32min after RH breakout, and the molten steel casting superheat temperature in a continuous casting process is 20 C.
[070] (2) Vacuum welding combined blank making: after surfaces of the continuous casting blanks are milled and ground, electron beam welding and combination are carried out in a vacuum chamber, a blank compounding manner is to compound two blanks, the compound blank is made by using a disclosed conventional process, and a thickness of the obtained compound blank is 868mm.
[071] (3) Compound blank cogging and rolling: the compound blank is heated by a soaking furnace, and while the segregation of the blanks is fully diffused, partial metallurgical bonding of compound interfaces is completed through high-temperature diffusion; and a single-stand high-permeability rolling process is adopted in a roughing mill, rolling passes are reasonably allocated, repeated recrystallization is carried out to enable the compound interfaces to achieve firm metallurgical bonding, a thickness of an intermediate blank is 440mm, and after rolled and discharged from the production line, the blank enters the cover to be slowly cooled for 72 h to fully diffuse hydrogen.
[072] Further, the compound blank adopts a sectional heating process: the steel is charged at 530 C, and the steel is sealed for 2 hours; in a low temperature section, the temperature rises to 830 C at a speed of 65 C/h, and is kept for 4.5 hours; in a medium temperature section, the temperature rises to 1020 C at a speed of 105 C/h, and is kept for 2 hours; and in a high temperature section, a temperature rise speed is not limited, and the temperature rises to 1242 C, and is kept for 10 hours.
[073] Further, a main task of a compound blank cogging process is to complete rolling and compounding on the roughing mill to obtain the intermediate blank with a reasonable size, an initial rolling temperature is 1070 C, a finish rolling temperature is 975 C, a high-permeability rolling process is adopted, a single-pass rolling reduction of 4 rolling passes in longitudinal rolling passes is 50 mm, being 55 mm, 55 mm, 55 mm and 52 mm respectively.
[074] After discharged from the production line, the steel plate is added with a cover to be slowly cooled for 72 hours.
[075] (4) Finished steel plate rolling: after the intermediate blank is slowly cooled and finished, heating is carried out again in a walking heating furnace to make the intermediate blank completely austenitized, segregation defects in a core of the blank is further reduced through second-time high-temperature diffusion heating, and at the same time, convenience is provided for achieving second-time high-permeability rolling. Further, the intermediate blank adopts a sectional heating manner: the total heating time is 620 min, the temperature of a second heating section is 1200-1250 C, the temperature of a soaking section is 1180-1250 C, and the total heating time of the second heating section and the soaking section is 310min to ensure that the segregation of the casting blanks is fully diffused.
[076] Rolling is divided into two stages: rough rolling and finish rolling;
rolling deformation is mainly concentrated in the rough rolling stage, the high-permeability rolling process is adopted in the stage, and a single-pass rolling reduction of 2 rolling passes is 50 mm, being 55 mm and 55 mm respectively; a main task of the finish rolling is to accurately control a thickness tolerance and obtain a good plate shape, an initial rolling temperature of finish rolling is 810 C, and a stand-by thickness is 270 mm; and after discharged from the production line, the steel plate is stacked to be slowly cooled for 48 hours to fully diffuse hydrogen.
rolling deformation is mainly concentrated in the rough rolling stage, the high-permeability rolling process is adopted in the stage, and a single-pass rolling reduction of 2 rolling passes is 50 mm, being 55 mm and 55 mm respectively; a main task of the finish rolling is to accurately control a thickness tolerance and obtain a good plate shape, an initial rolling temperature of finish rolling is 810 C, and a stand-by thickness is 270 mm; and after discharged from the production line, the steel plate is stacked to be slowly cooled for 48 hours to fully diffuse hydrogen.
[077] (5) Heat treatment: the steel plate is normalized and tempered in turn, and water accelerated cooling is adopted in a water tank after normalizing.
[078] Further, a normalizing heating temperature is 900 C, a temperature keeping time coefficient is 2.2min/mm, and the steel plate is taken out of a furnace and cooled by water, so that the surface of the steel plate is cooled to 420 C; in order to prevent the strength of the steel plate from being greatly reduced, a tempering temperature of the steel plate is not lower than that of the simulated post-weld heat treatment; and for tempering, a tempering temperature is 620 C, and the temperature keeping time coefficient is 4.0min/mm.
[079] The hydrogen-induced cracking-resistant steel plate with the thickness of 230mm for the pressure vessel, produced by the above-mentioned manufacturing process, has well-matched mechanical properties and excellent hydrogen-induced cracking resistance. The mechanical properties of the steel plate are shown in Table 1 in detail, and the hydrogen-induced cracking resistance is shown in Table 2. The flaw detection of the steel plate meets requirements of Level TI of the NB/T47013.3 standard.
[080] Embodiment 3
[081] A thickness of a hydrogen-induced cracking-resistant steel plate for a pressure vessel in the embodiment is 250mm, and chemical compositions of the hydrogen-induced cracking-resistant steel plate for the pressure vessel include, by weight percentage: C: 0.13%, Si: 0.32%, Mn: 1.32%, P: 0.004%, S: 5 0.0005%, Cr: 0.22%, Ni: 0.36%, Mo:
0.11%, Alt: 0.028%, Nb: 0.018%, V: 0.025%, Ti: 0.016%, and the rest being Fe and inevitable impurity elements, a carbon equivalent Ceq 5 0.45%, and Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15.
0.11%, Alt: 0.028%, Nb: 0.018%, V: 0.025%, Ti: 0.016%, and the rest being Fe and inevitable impurity elements, a carbon equivalent Ceq 5 0.45%, and Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15.
[082] A manufacturing process of the steel plate is as follows:
The steel plate product of the present invention is produced by a compound blank, and the main process steps are successively continuous casting blank smelting and casting, vacuum welding combined blank making, compound blank cogging and rolling, finished steel plate rolling, and heat treatment. The specific operations are as follows:
The steel plate product of the present invention is produced by a compound blank, and the main process steps are successively continuous casting blank smelting and casting, vacuum welding combined blank making, compound blank cogging and rolling, finished steel plate rolling, and heat treatment. The specific operations are as follows:
[083] (1) Continuous casting blank smelting and casting
[084] 450 mm section continuous casting blanks with the same size produced by a same smelting furnace number are taken as blanks of a compound blank, the continuous casting blanks adopt a pure steel smelting process, measures such as large tundish casting and prolonging of the soft argon gas blowing time are taken to make non-metallic inclusions fully float to slag, so that a content of the non-metallic inclusions in steel is reduced, the purity of molten steel is improved, and the non-metallic inclusions of Class A, Class B, Class C and Class D in the molten steel are controlled to be 5 1.0 grade in individual item and 5 2.5 grade in sum; through a low superheat argon protection casting process and a dynamic soft reduction technology, segregation of the continuous casting blanks is controlled to be below 1.0 grade for Class C and porosity is controlled to be below 0.5 grade; and after discharged from a production line, the continuous casting blanks are added with a cover to be slowly cooled for 72 h to fully diffuse hydrogen.
[085] Further, production technology processes of the continuous casting blanks are:
KR pretreatment ¨> converter smelting ¨> LF refining ¨> RH refining ¨>
continuous casting. The converter smelting is followed by slag-off treatment, the soft argon gas blowing time is 38min after RH breakout, and the molten steel casting superheat temperature in a continuous casting process is 23 C.
KR pretreatment ¨> converter smelting ¨> LF refining ¨> RH refining ¨>
continuous casting. The converter smelting is followed by slag-off treatment, the soft argon gas blowing time is 38min after RH breakout, and the molten steel casting superheat temperature in a continuous casting process is 23 C.
[086] (2) Vacuum welding combined blank making: after surfaces of the continuous casting blanks are milled and ground, electron beam welding and combination are carried out in a vacuum chamber, a blank compounding manner is to compound two blanks, the compound blank is made by using a disclosed conventional process, and a thickness of the obtained compound blank is 870mm.
[087] (3) Compound blank cogging and rolling: the compound blank is heated by a soaking furnace, and while the segregation of the blanks is fully diffused, partial metallurgical bonding of compound interfaces is completed through high-temperature diffusion; and a single-stand high-permeability rolling process is adopted in a roughing mill, rolling passes are reasonably allocated, repeated recrystallization is carried out to enable the compound interfaces to achieve firm metallurgical bonding, a thickness of an intermediate blank is 450mm, and after rolled and discharged from the production line, the blank enters the cover to be slowly cooled for 72 h to fully diffuse hydrogen.
[088] Further, the compound blank adopts a sectional heating process: the steel is charged below 545 C, and the steel is sealed for 2 hours; in a low temperature section, the temperature rises to 820 C at a speed of 60 C/h, and is kept for 4 hours; in a medium temperature section, the temperature rises to 1020 C at a speed of 110 C/h, and is kept for 2 h;
and in a high temperature section, a temperature rise speed is not limited, and the temperature rises to 1250 C, and is kept for 12 hours.
and in a high temperature section, a temperature rise speed is not limited, and the temperature rises to 1250 C, and is kept for 12 hours.
[089] Further, a main task of a compound blank cogging process is to complete rolling and compounding on the roughing mill to obtain the intermediate blank with a reasonable size, an initial rolling temperature is 1100 C, a finish rolling temperature is 980 C, a high-permeability rolling process is adopted, a single-pass rolling reduction of 4 rolling passes in longitudinal rolling passes is 50 mm, being 55 mm, 55 mm, 55 mm and 55mm respectively.
[090] After discharged from the production line, the steel plate is added with a cover to be slowly cooled for 72 hours.
[091] (4) Finished steel plate rolling: after the intermediate blank is slowly cooled and finished, heating is carried out again in a walking heating furnace to make the intermediate blank completely austenitized, segregation defects in a core of the blank is further reduced through second-time high-temperature diffusion heating, and at the same time, convenience is provided for achieving second-time high-permeability rolling. Further, the intermediate blank adopts a sectional heating manner: the total heating time is 620 min, the temperature of a second heating section is 1200-1250 C, the temperature of a soaking section is 1180-1250 C, and the total heating time of the second heating section and the soaking section is 320min to ensure that the segregation of the casting blanks is fully diffused.
[092] Rolling is divided into two stages: rough rolling and finish rolling;
rolling deformation is mainly concentrated in the rough rolling stage, the high-permeability rolling process is adopted in the stage, and a single-pass rolling reduction of 2 rolling passes is 50 mm, being 56mm and 56mm respectively; a main task of the finish rolling is to accurately control a thickness tolerance and obtain a good plate shape, an initial rolling temperature of finish rolling is 800 C, and a stand-by thickness is 280mm; and after discharged from the production line, the steel plate is stacked to be slowly cooled for 48 hours to fully diffuse hydrogen.
rolling deformation is mainly concentrated in the rough rolling stage, the high-permeability rolling process is adopted in the stage, and a single-pass rolling reduction of 2 rolling passes is 50 mm, being 56mm and 56mm respectively; a main task of the finish rolling is to accurately control a thickness tolerance and obtain a good plate shape, an initial rolling temperature of finish rolling is 800 C, and a stand-by thickness is 280mm; and after discharged from the production line, the steel plate is stacked to be slowly cooled for 48 hours to fully diffuse hydrogen.
[093] (5) Heat treatment: the steel plate is normalized and tempered in turn, and water accelerated cooling is adopted in a water tank after normalizing.
[094] Further, a normalizing heating temperature is 900 C, a temperature keeping time coefficient is 2.5min/mm, and the steel plate is taken out of a furnace and cooled by water, so that the surface of the steel plate is cooled to 400 C; in order to prevent the strength of the steel plate from being greatly reduced, a tempering temperature of the steel plate is not lower than that of the simulated post-weld heat treatment; and for tempering, a tempering temperature is 610 C, and the temperature keeping time coefficient is 4.5min/mm.
[095] The hydrogen-induced cracking-resistant steel plate with the thickness of 250 mm for the pressure vessel, produced by the above-mentioned manufacturing process, has well-matched mechanical properties and excellent hydrogen-induced cracking resistance. The mechanical properties of the steel plate are shown in Table 1 in detail, and the hydrogen-induced cracking resistance is shown in Table 2. The flaw detection of the steel plate meets requirements of Level TI of the NB/T47013.3 standard. The metallographic structure of the steel plate is ferrite + tempered bainite, and the microstructure morphology is shown in Figures 1-3.
Table 1 Mechanical properties of steel plate produced by each Embodiment -30 C Charpy Z-direction V-shaped Surface Plate Yield Tensile tensile Sample Elongation, impact Brinell Embodiment thickness, Sample status Sampling strength, strength, section direction %
energy hardness, mm position MPa MPa absorption shrinkage, HB
%
Thickness 178,175,182 Normalizing + 1/4 water Thickness accelerated 342 545 32 208,194,167 65,65,68 178,177,178 cooling +
tempering Thickness 166,162,188 1 210 Horizontal Normalizing + Thickness 330 531 31 164,152,174 water 1/4 accelerated Thickness 322 525 30 196,182,175 cooling + 1/2 62,65,65 174,172,172 tempering +
simulated Thickness 328 522 29 154,162,185 post-weld heat 3/4 treatment Normalizing + Thickness 346 548 30 168,145,132 2 230 Horizontal water 1/4 62,62,66 176,174,175 accelerated Thickness 340 542 30 197,164,168 cooling + 1/2 tempering Thickness 341 544 31 146,152,108 Normalizing + Thickness 330 531 28 127,155,132 water 1/4 accelerated Thickness 322 525 30 148,164,168 cooling + 1/2 __________________________________________________ 61,61,60 170,171,172 tempering +
simulated Thickness 328 522 29 115,122,127 post-weld heat 3/4 treatment Thickness 338 552 30 138,105,122 Normalizing +
water Thickness 342 545 32 153,154,145 60,64,58 174,177,175 accelerated cooling +
tempering Thickness 345 548 31 134,114,109 3 250 Horizontal Normalizing + Thickness 325 527 30 128,115,102 water 1/4 accelerated Thickness 330 529 32 116,115,135 cooling + 1/2 57,58,62 172,167,172 tempering +
simulated Thickness 327 526 31 107,121,113 post-weld heat 3/4 treatment Note: simulated post-weld heat treatment: 610 10 C x 30 h.
Table 2 Hydrogen-induced cracking (HIC) resistance of steel plates produced in various embodiments Embodiment Section 1 Section 2 Section 3 Hydrogen Sample bubbling No. CSR% CLR% CTR% CSR% CLR% CLR% CTR% CSR% CLR%
(HB) Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none 1 Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none 2 Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none 3 Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none
Table 1 Mechanical properties of steel plate produced by each Embodiment -30 C Charpy Z-direction V-shaped Surface Plate Yield Tensile tensile Sample Elongation, impact Brinell Embodiment thickness, Sample status Sampling strength, strength, section direction %
energy hardness, mm position MPa MPa absorption shrinkage, HB
%
Thickness 178,175,182 Normalizing + 1/4 water Thickness accelerated 342 545 32 208,194,167 65,65,68 178,177,178 cooling +
tempering Thickness 166,162,188 1 210 Horizontal Normalizing + Thickness 330 531 31 164,152,174 water 1/4 accelerated Thickness 322 525 30 196,182,175 cooling + 1/2 62,65,65 174,172,172 tempering +
simulated Thickness 328 522 29 154,162,185 post-weld heat 3/4 treatment Normalizing + Thickness 346 548 30 168,145,132 2 230 Horizontal water 1/4 62,62,66 176,174,175 accelerated Thickness 340 542 30 197,164,168 cooling + 1/2 tempering Thickness 341 544 31 146,152,108 Normalizing + Thickness 330 531 28 127,155,132 water 1/4 accelerated Thickness 322 525 30 148,164,168 cooling + 1/2 __________________________________________________ 61,61,60 170,171,172 tempering +
simulated Thickness 328 522 29 115,122,127 post-weld heat 3/4 treatment Thickness 338 552 30 138,105,122 Normalizing +
water Thickness 342 545 32 153,154,145 60,64,58 174,177,175 accelerated cooling +
tempering Thickness 345 548 31 134,114,109 3 250 Horizontal Normalizing + Thickness 325 527 30 128,115,102 water 1/4 accelerated Thickness 330 529 32 116,115,135 cooling + 1/2 57,58,62 172,167,172 tempering +
simulated Thickness 327 526 31 107,121,113 post-weld heat 3/4 treatment Note: simulated post-weld heat treatment: 610 10 C x 30 h.
Table 2 Hydrogen-induced cracking (HIC) resistance of steel plates produced in various embodiments Embodiment Section 1 Section 2 Section 3 Hydrogen Sample bubbling No. CSR% CLR% CTR% CSR% CLR% CLR% CTR% CSR% CLR%
(HB) Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none 1 Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none 2 Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none 3 Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none Sample 0 0 0 0 0 0 0 none
[096] In addition to the above embodiments, the present invention also includes other implementations, and all technical solutions formed by equivalent transformation or equivalent replacement shall fall within the protection scope of the claims of the present invention.
Claims (9)
1. A hydrogen-induced cracking-resistant steel plate with a thickness of > 200-250 mm for a pressure vessel, characterized in that, the steel plate has a chemical composition comprising, by weight percentage, C: 0.10-0.20%, Si: 0.15-0.40%, Mn: 0.95-1.35%, P: ~
0.005%, S: ~
0.0008%, Cr: 0.10-0.30%, Ni: 0.25-0.40%, Mo: 0.08-0.12%, Alt: 0.02-0.05%, Nb:
0.01-0.02%, V:
0.01-0.03%, Ti: 0.01-0.02%, B: ~ 0.0005%, and balance being Fe and inevitable impurity elements.
0.005%, S: ~
0.0008%, Cr: 0.10-0.30%, Ni: 0.25-0.40%, Mo: 0.08-0.12%, Alt: 0.02-0.05%, Nb:
0.01-0.02%, V:
0.01-0.03%, Ti: 0.01-0.02%, B: ~ 0.0005%, and balance being Fe and inevitable impurity elements.
2. The hydrogen-induced cracking-resistant steel plate of Claim 1, characterized in that, the chemical composition of the steel plate has a carbon equivalent (Ceq) ~
0.45%, wherein Ceq=C+Mn/6 +(Cr+Mo+V)/5+(Ni+Cu)/15.
0.45%, wherein Ceq=C+Mn/6 +(Cr+Mo+V)/5+(Ni+Cu)/15.
3. A method for manufacturing the hydrogen-induced cracking-resistant steel plate of Claim 1, characterized in that, an entire preparation method comprises continuous casting blank smelting and casting, vacuum welding compound blank forming, compound blank cogging and rolling, finished steel plate rolling, and heat treatment.
4. The method of Claim 3, characterized in that, the method specifically comprises the following steps:
1) using continuous casting slabs with the same cross-sectional size produced by a same smelting furnace as blanks for a compound blank, wherein the continuous casting blanks are produced using a pure steel smelting process, and measures including large tundish casting and prolonged soft argon gas blowing time, to allow non-metallic inclusions to fully float to slag, so as to reduce a content of non-metallic inclusions in steel, increase a purity of molten steel, and control the non-metallic inclusions of Class A, Class B, Class C
and Class D in the molten steel to be ~ 1.0 grade for each one of the classes and ~ 2.5 grade in total; a low superheat argon protection casting process and a dynamic soft reduction technology to control segregation in the continuous casting blanks to be below 1.0 grade for Class C
and porosity to be below 0.5 grade; and after discharged from a production line, covering and slowly cooling the continuous casting blanks for 72 hours to fully diffuse hydrogen;
2) after surfaces of the continuous casting blanks are milled and ground, carrying out electron beam welding and combination in a vacuum chamber, wherein slab compounding comprises compounding two slabs to form the compound blank;
3) heating the compound blank by a soaking furnace, and while the segregation in the blanks is fully diffused, completing the partial metallurgical bonding of compound interfaces through high-temperature diffusion; and adopting a single-stand high-permeability rolling process in a roughing mill, reasonably allocating rolling passes, carrying out repeated recrystallization to enable the compound interfaces to achieve firm metallurgical bonding, controlling a thickness of an intermediate blank to be 400-450 mm, and after rolled and discharged from the production line, covering and slowly cooling the intermediate blank for 72 hours to fully diffuse hydrogen;
4) after the intermediate blank has been slowly cooled and finished, heating again in a walking furnace to make the intermediate blank completely austenitized, further reducing segregation defects in a core of the intermediate blank through second-time high-temperature diffusion heating, and at the same time, providing convenience for achieving second-time high-permeability rolling; and 5) performing normalizing and tempering treatment the steel plate in turn, and adopting water accelerated cooling in a water tank after normalizing.
1) using continuous casting slabs with the same cross-sectional size produced by a same smelting furnace as blanks for a compound blank, wherein the continuous casting blanks are produced using a pure steel smelting process, and measures including large tundish casting and prolonged soft argon gas blowing time, to allow non-metallic inclusions to fully float to slag, so as to reduce a content of non-metallic inclusions in steel, increase a purity of molten steel, and control the non-metallic inclusions of Class A, Class B, Class C
and Class D in the molten steel to be ~ 1.0 grade for each one of the classes and ~ 2.5 grade in total; a low superheat argon protection casting process and a dynamic soft reduction technology to control segregation in the continuous casting blanks to be below 1.0 grade for Class C
and porosity to be below 0.5 grade; and after discharged from a production line, covering and slowly cooling the continuous casting blanks for 72 hours to fully diffuse hydrogen;
2) after surfaces of the continuous casting blanks are milled and ground, carrying out electron beam welding and combination in a vacuum chamber, wherein slab compounding comprises compounding two slabs to form the compound blank;
3) heating the compound blank by a soaking furnace, and while the segregation in the blanks is fully diffused, completing the partial metallurgical bonding of compound interfaces through high-temperature diffusion; and adopting a single-stand high-permeability rolling process in a roughing mill, reasonably allocating rolling passes, carrying out repeated recrystallization to enable the compound interfaces to achieve firm metallurgical bonding, controlling a thickness of an intermediate blank to be 400-450 mm, and after rolled and discharged from the production line, covering and slowly cooling the intermediate blank for 72 hours to fully diffuse hydrogen;
4) after the intermediate blank has been slowly cooled and finished, heating again in a walking furnace to make the intermediate blank completely austenitized, further reducing segregation defects in a core of the intermediate blank through second-time high-temperature diffusion heating, and at the same time, providing convenience for achieving second-time high-permeability rolling; and 5) performing normalizing and tempering treatment the steel plate in turn, and adopting water accelerated cooling in a water tank after normalizing.
5. The method of Claim 4, characterized in that, production technology processes of the continuous casting blanks comprise: KR pretreatment ¨> converter smelting ¨>
LF refining¨>
RH refining ¨> continuous casting, wherein the converter smelting is followed by slag-off treatment, the soft argon gas blowing time is longer than 30 min after RH
breakout, a molten steel casting superheat temperature in the continuous casting is 10-30 C, further 10-25 C.
LF refining¨>
RH refining ¨> continuous casting, wherein the converter smelting is followed by slag-off treatment, the soft argon gas blowing time is longer than 30 min after RH
breakout, a molten steel casting superheat temperature in the continuous casting is 10-30 C, further 10-25 C.
6. The method of Claim 4, characterized in that, the compound blank is heated in stages, wherein: the compound blank is charged into the walking furnace at a temperature below 550 C and the furnace is sealed for 1-2 hours; at a low temperature stage, the temperature is increased to 820 20 C at a rate of not more than 75 C/h, and maintained for 3-5 hours; at a medium temperature stage, the temperature is creased to 1000 20 C at a rate of not more than 110 C/h, and maintained for 2 hours; and at a high temperature stage, the temperature is increased at an unlimited rate to 1220-1250 C, and maintained for 8-12 hours.
7. The method of Claim 4, characterized in that, the compound blank cogging comprises rolling and compounding on the roughing mill to obtain the intermediate blank, an initial rolling temperature is 1060-1100 C, a finish rolling temperature is 950-980 C, a high-permeability rolling process is adopted, a single-pass rolling reduction of at least 4 rolling passes in longitudinal rolling passes is 50 mm, and after discharged from the production line, the steel plate is covered and slowly cooled for 72 hours.
8. The method of Claim 4, characterized in that, the intermediate blank is heated in stages, wherein the total heating time is 620 min, a heating temperature in a second heating stage is 1200-1250 C, a heating temperature in a soaking stage is 1180-1250 C, a total heating time of the second heating stage and the soaking stage is 270 min to allow the segregation in the casting blanks to be fully diffused; the rolling comprises two stages, a rough rolling stage and a finish rolling stage, wherein rolling deformation mainly occurs in the rough rolling stage, the high-permeability rolling process being adopted in the rough rolling stage, and a single-pass rolling reduction of at least 2 rolling passes being 50 mm; a main task of the finish rolling stage is to accurately control a thickness tolerance and obtain a good plate shape, an initial rolling temperature at the finish rolling stage being 820 20 C, and a stand-by thickness is a thickness of a finished steel plate + 30 mm; and after discharged from the production line, the steel plate is stacked and slowly cooled for 48 hours to fully diffuse hydrogen.
9. The method of Claim 4, characterized in that, a normalizing heating temperature is 880-910 C with a temperature holding time coefficient of 2.0-2.5 min/mm, the steel plate being taken out of the soaking furnace is cooled with water to cool a surface of the steel plate to 400-500 C; and a tempering temperature is 610-630 C with a temperature holding time coefficient of 3.5-4.5 min/mm.
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| CN202110352973.1A CN113278878B (en) | 2021-04-01 | 2021-04-01 | Hydrogen-induced cracking resistant pressure vessel steel plate with thickness of more than 200-250 mm and manufacturing method thereof |
| CN202110352973.1 | 2021-04-01 | ||
| PCT/CN2021/131773 WO2022205939A1 (en) | 2021-04-01 | 2021-11-19 | Hydrogen-induced-cracking-resistant pressure vessel steel plate with thickness greater than 200-250 mm and manufacturing method therefor |
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| CA (1) | CA3194605A1 (en) |
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| CN115595506B (en) * | 2022-11-01 | 2024-04-09 | 伊莱特能源装备股份有限公司 | High-quality low-alloy high-strength plate steel forging and preparation method thereof |
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| WO2022205939A1 (en) | 2022-10-06 |
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