CN114921619A - Steelmaking method capable of improving delayed cracking resistance of hot formed steel in CSP production line - Google Patents
Steelmaking method capable of improving delayed cracking resistance of hot formed steel in CSP production line Download PDFInfo
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- CN114921619A CN114921619A CN202210562344.6A CN202210562344A CN114921619A CN 114921619 A CN114921619 A CN 114921619A CN 202210562344 A CN202210562344 A CN 202210562344A CN 114921619 A CN114921619 A CN 114921619A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 92
- 239000010959 steel Substances 0.000 title claims abstract description 92
- 238000005336 cracking Methods 0.000 title claims abstract description 47
- 230000003111 delayed effect Effects 0.000 title claims abstract description 46
- 238000000034 method Methods 0.000 title claims abstract description 38
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 25
- 238000009628 steelmaking Methods 0.000 title claims abstract description 12
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 26
- 238000010438 heat treatment Methods 0.000 claims abstract description 18
- 238000005266 casting Methods 0.000 claims abstract description 13
- 238000003723 Smelting Methods 0.000 claims abstract description 12
- 229910052742 iron Inorganic materials 0.000 claims abstract description 12
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims abstract description 11
- 239000011575 calcium Substances 0.000 claims abstract description 11
- 229910052791 calcium Inorganic materials 0.000 claims abstract description 11
- 238000000137 annealing Methods 0.000 claims abstract description 10
- 238000005097 cold rolling Methods 0.000 claims abstract description 10
- 238000001816 cooling Methods 0.000 claims abstract description 9
- 238000009489 vacuum treatment Methods 0.000 claims abstract description 9
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims abstract description 8
- 238000007670 refining Methods 0.000 claims abstract description 7
- 230000003009 desulfurizing effect Effects 0.000 claims abstract description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 5
- 238000010791 quenching Methods 0.000 claims abstract description 4
- 230000000171 quenching effect Effects 0.000 claims abstract description 4
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 30
- 230000008569 process Effects 0.000 claims description 25
- 238000007664 blowing Methods 0.000 claims description 18
- 229910052786 argon Inorganic materials 0.000 claims description 15
- 239000002893 slag Substances 0.000 claims description 14
- 238000005096 rolling process Methods 0.000 claims description 8
- 238000009749 continuous casting Methods 0.000 claims description 6
- 238000005098 hot rolling Methods 0.000 claims description 6
- 239000002245 particle Substances 0.000 claims description 5
- 238000005554 pickling Methods 0.000 claims description 4
- 238000005275 alloying Methods 0.000 claims description 3
- 238000005520 cutting process Methods 0.000 claims description 3
- 230000009467 reduction Effects 0.000 claims description 3
- 238000010079 rubber tapping Methods 0.000 claims description 3
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims 1
- 229910052593 corundum Inorganic materials 0.000 claims 1
- 229910001845 yogo sapphire Inorganic materials 0.000 claims 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 abstract description 24
- 239000001257 hydrogen Substances 0.000 abstract description 24
- 229910052739 hydrogen Inorganic materials 0.000 abstract description 24
- 230000035945 sensitivity Effects 0.000 abstract description 11
- 230000001788 irregular Effects 0.000 abstract description 6
- 238000009826 distribution Methods 0.000 abstract description 4
- 239000002253 acid Substances 0.000 abstract description 2
- 238000005406 washing Methods 0.000 abstract description 2
- 238000007796 conventional method Methods 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 8
- 238000012360 testing method Methods 0.000 description 8
- 229910052758 niobium Inorganic materials 0.000 description 7
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 6
- 229910052750 molybdenum Inorganic materials 0.000 description 6
- 229910052804 chromium Inorganic materials 0.000 description 5
- 239000012535 impurity Substances 0.000 description 5
- 238000002360 preparation method Methods 0.000 description 5
- 239000000126 substance Substances 0.000 description 5
- 229910052796 boron Inorganic materials 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 229910052717 sulfur Inorganic materials 0.000 description 4
- 229910052719 titanium Inorganic materials 0.000 description 4
- 229910052720 vanadium Inorganic materials 0.000 description 4
- HEMHJVSKTPXQMS-UHFFFAOYSA-M Sodium hydroxide Chemical compound [OH-].[Na+] HEMHJVSKTPXQMS-UHFFFAOYSA-M 0.000 description 3
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 3
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 238000005452 bending Methods 0.000 description 3
- 238000012512 characterization method Methods 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- 238000004220 aggregation Methods 0.000 description 2
- 230000002776 aggregation Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 239000010410 layer Substances 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000011056 performance test Methods 0.000 description 2
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- XFWJKVMFIVXPKK-UHFFFAOYSA-N calcium;oxido(oxo)alumane Chemical compound [Ca+2].[O-][Al]=O.[O-][Al]=O XFWJKVMFIVXPKK-UHFFFAOYSA-N 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- NFFIWVVINABMKP-UHFFFAOYSA-N methylidynetantalum Chemical compound [Ta]#C NFFIWVVINABMKP-UHFFFAOYSA-N 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000033764 rhythmic process Effects 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 229910003468 tantalcarbide Inorganic materials 0.000 description 1
- 229910052715 tantalum Inorganic materials 0.000 description 1
- 238000003856 thermoforming Methods 0.000 description 1
- RMLPZKRPSQVRAB-UHFFFAOYSA-N tris(3-methylphenyl) phosphate Chemical compound CC1=CC=CC(OP(=O)(OC=2C=C(C)C=CC=2)OC=2C=C(C)C=CC=2)=C1 RMLPZKRPSQVRAB-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/04—Removing impurities by adding a treating agent
- C21C7/064—Dephosphorising; Desulfurising
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
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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
- B22D11/10—Supplying or treating molten metal
- B22D11/11—Treating the molten metal
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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
- B22D11/12—Accessories for subsequent treating or working cast stock in situ
- B22D11/128—Accessories for subsequent treating or working cast stock in situ for removing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C1/00—Refining of pig-iron; Cast iron
- C21C1/02—Dephosphorising or desulfurising
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/0056—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00 using cored wires
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/04—Removing impurities by adding a treating agent
- C21C7/06—Deoxidising, e.g. killing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/10—Handling in a vacuum
-
- 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
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold 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
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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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- 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
- 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
- B21B2001/221—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by cold-rolling
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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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- Organic Chemistry (AREA)
- Mechanical Engineering (AREA)
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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Treatment Of Steel In Its Molten State (AREA)
Abstract
A steelmaking method capable of improving delayed cracking resistance of hot formed steel in CSP production line production comprises the following steps: desulfurizing molten iron; the method is conventional; smelting; LF refining; RH vacuum treatment; casting into a blank; heating a casting blank; cooling the laminar flow and then coiling; cold rolling after conventional acid washing; annealing the product; heating and austenitizing under the protection of nitrogen after blanking; and (4) after hot stamping and forming, quenching the blank by a conventional method, and naturally cooling the blank to room temperature. According to the invention, Al is added by feeding calcium in an amount of 0.15-0.40 kg/ton steel 2 O 3 The maximum size of the inclusion is reduced from about 20 mu m to not more than 10 mu m, the inclusion is changed from irregular inclusion to spherical inclusion, and the distribution density is changed from 4.63/mm 2 Down to not more than 0.8 pieces/mm 2 The hydrogen-induced delayed cracking sensitivity of the steel is reduced to less than or equal to 50 percent from the original 80 percent.
Description
Technical Field
The invention relates to a production method of steel for automobiles, in particular to a steelmaking method capable of improving the delayed cracking resistance of hot forming steel in CSP production line production.
Background
According to statistics, the fuel efficiency can be improved by 6-8% when the weight of the automobile is reduced by 10%. One of the most important ways for lightening the automobile is to adopt high-strength and ultrahigh-strength steel, the existing hot forming steel is the most widely applied ultrahigh-strength steel, the strength level is 1300-2000 MPa, and the steel is mainly applied to the A column, the B column, the front and rear bumpers, the automobile door anti-collision beam, the middle channel and other parts. However, when the strength of the steel exceeds 1000MPa, the delayed cracking problem of the steel also occurs, and a great deal of research has proved that the delayed cracking of the steel is caused by hydrogen in materials and the service environment of the materials, has unpredictability and abruptness, often causes serious safety problems, and therefore, the delayed cracking problem of the steel becomes a problem which must be solved by the light weight of the automobile.
The current hot formed steels are mainly MnB series steels, which are deoxidized mainly with Al during smelting. Therefore, the inclusions in the steel generate Al by deoxidation of Al in addition to TiN 2 O 3 And (4) inclusion. Generated Al 2 O 3 The inclusions not only have high hardness, high melting point and irregular shape, are easy to cluster into large inclusions, but also have sharp edges and corners, can generate larger stress with a steel matrix in steel, and Al 2 O 3 The inclusion also has high hydrogen binding energy (about 72KJ/mol), easy hydrogen capture and a hydrogen aggregation coefficient as high as 17. The accumulation of large amounts of hydrogen also leads to delayed cracking of the steel, so Al 2 O 3 The inclusions become a crack source for delayed cracking, and the cracking sensitivity of the steel is very high, compared to the stress of the spherical inclusions and the matrix. The delayed cracking resistance of the steel is critical.
From the retrieved prior art:
most of the literature only focuses on the basic mechanical properties of hot-formed steel, and little is known about Al in steel 2 O 3 The hazards of inclusions to delayed cracking of hot formed steel, and how to deal with, for example:
chinese patent application No. CN202110888137.5 discloses 1700 MPa-grade hydrogen-induced delayed cracking resistant hot forming steel and a preparation method thereof, relating to the technical field of automobile ultrahigh-strength steel. The hot forming steel comprises the following chemical components in percentage by mass: c: 0.21 to 0.24%, Si: 0.27 to 0.34%, Mn: 1.1-1.3%, S: less than or equal to 0.005%, P: less than or equal to 0.01 percent, Al: 0.02-0.05%, Cr: 0.15-0.2%, B: 0.002-0.003%, Ta: 0.02-0.06%, Fe: the balance; the preparation method comprises the following steps: desulfurizing molten iron, smelting in a converter, casting into a blank, heating and homogenizing the blank, hot rolling, coiling, pickling, cold rolling and hot stamping. According to the invention, by adding trace Ta and controlling the processing technology, a nanoscale tantalum carbide precipitated phase is formed in the steel and grains are refined, so that the strength, the plasticity and the hydrogen-induced delayed cracking resistance of the steel are synergistically improved. The element ta used in the document is a rare element, which can greatly increase the production cost, the element ta can seriously reduce the welding performance of steel, and the element ta is rarely used in the metallurgical industry, and meanwhile, the method does not pay attention to the influence of the steelmaking process on the delayed cracking performance of the product.
The Chinese patent publication No. CN 110306123A discloses a high-toughness hot forming steel with tensile strength more than or equal to 1800MPa and a production method thereof, and the high-toughness hot forming steel comprises the following components in percentage by mass: 0.29-0.35% of C, less than or equal to 0.5% of Si, 0.5-1.5% of Mn, less than or equal to 0.020% of P, less than or equal to 0.010% of S, less than or equal to 0.50% of Cr, 0.01-0.06% of Al, 0.01-0.06% of Nb0.01-0.06% of V, less than or equal to 0.5% of Mo, and the balance of Fe and inevitable impurities; the production process comprises the following steps: firstly, smelting; secondly, casting blanks; thirdly, hot rolling; fourthly, cold rolling; fifthly, annealing; sixthly, thermoforming. The method uses more precious alloys Mo, Nb and V to obviously increase the production cost, and does not describe the hydrogen-induced delayed cracking resistance and the principle thereof, nor perform relevant characterization on the delayed cracking resistance.
Chinese patent publication No. CN 110423953 discloses a hot-formed member with excellent cold bending performance and tensile strength of more than 1800MPa and a preparation method thereof, wherein the hot-formed member comprises the following chemical components in percentage by weight: c: 0.29-0.35%, Si: less than or equal to 0.5 percent, Mn: 0.5-1.5%, P: less than or equal to 0.020%, S: less than or equal to 0.010%, Cr: less than or equal to 0.50%, Al: 0.01-0.06%, Nb: 0.01-0.06%, V: 0.01-0.06%, Mo: less than or equal to 0.5 percent, and the balance of Fe and inevitable impurities; the surface layer of the hot forming component is a soft-phase ferrite structure, the inner layer is a martensite structure, and the grain size is less than or equal to 10 mu m. The hot forming steel with high toughness and uniform structure with the tensile strength of more than or equal to 1800MPa is obtained by adopting the component design of low Si, low Mn, low Cr, no Ti, no B and Mo, combining TMCP, continuous annealing and hot forming processes, and the decarburized layer with the thickness of 15-25 mu m is obtained after hot rolling by controlling the preparation process in the preparation process, so that the cold bending performance of the hot forming component is improved. The document aims to improve the toughness and the cold bending property of a component through special component design, the use of more noble alloys Mo, Nb and V can obviously increase the production cost, and meanwhile, the document does not describe the hydrogen-induced delayed cracking resistance and the principle, does not perform relevant characterization on the delayed cracking resistance, and does not provide corresponding improvement measures or schemes.
Chinese patent publication No. CN 108754319A discloses hot forming steel with tensile strength more than or equal to 1800MPa produced by an ESP production line, and the components and wt% thereof are as follows: c: 0.28 to 0.40%, Si: 0.15 to 0.40%, Mn: 1.40-1.60%, P is less than or equal to 0.01%, S is less than or equal to 0.01%, Als: 0.015-0.050%, Cr is less than or equal to 0.80%, N is less than or equal to 0.005%, B: 0.002-0.005%, Mo less than or equal to 0.50%, Nb + Ti: 0.025 to 0.090%; the production method comprises the following steps: smelting and continuously casting into a plate blank; rough rolling; soaking; finish rolling after descaling under normal high pressure; laminar cooling; heating; and carrying out punch forming after acid washing. According to the invention, Nb and Ti are added compositely, Cr, B, Mo and other elements in the components are controlled, and an ESP short-flow process is adopted to produce the hot stamping forming steel with the tensile strength of 1800MPa, so that not only can the mechanical property of the hot stamping forming steel be ensured, but also the processes of repeatedly heating and uncoiling a plate coil and the like in the production process can be reduced, the processes of cold rolling and annealing heat treatment can be cancelled, the production cost is reduced, and how to reduce the delayed cracking sensitivity is not involved. The document aims at emphasizing that the ESP process is used for finishing product output and has lower cost, but the ESP product is a hot-rolled product, has poorer surface quality compared with the traditional cold-rolled product and is difficult to meet the higher surface quality requirement of the automobile industry, and meanwhile, the method does not describe the hydrogen-resistant delayed cracking performance and principle, does not pay attention to the influence of inclusions on delayed cracking, and does not carry out related characterization on the delayed cracking performance.
The document of chinese patent publication No. CN101275200A discloses "a hot-forming martensitic steel" mainly suitable for a steel for hot-press forming of thin parts having a tensile strength of 1.3 to 1.7 GPa. The main chemical components (weight percent) are as follows: 0.10-0.33% of C, 0.50-2.30% of Si, 0.50-2.00% of Mn, less than or equal to 0.020% of P, less than or equal to 0.015% of S, 0.015-0.060% of Al, less than or equal to 0.002% of [ O ], 0.002-0.015% of [ N ], and the balance of Fe and inevitable impurities. In addition, one or more of 0.0005 to 0.0050% of B, 0.02 to 0.10% of Ti, 0.02 to 0.10% of Nb, 0.02 to 0.15% of V, and 0.001 to 0.050% of RE is added. Compared with the existing hot-formed martensitic steel 22MnB5 steel, the steel disclosed by the document has the advantages that the tensile strength is improved to 1.3-1.7 GPa from 1.0-1.5 GPa, the steel has good plasticity, the elongation is more than 15%, and the hydrogen-induced delayed fracture sensitivity is obviously reduced, so that a foundation is provided for the light weight and high safety performance of an automobile. However, the document does not concern the effect of TiN inclusions on delayed cracking. The document mainly reduces the delayed cracking sensitivity by adding microalloy elements such as Nb, V, Ti and the like, but does not pay attention to the influence of TiN inclusions on delayed cracking, and has some defects. Secondly, mechanical tests using a bar-shaped test piece of phi 12 instead of a sheet test piece showed that these test steels were not sufficiently rolled, and the final rolled thickness was not less than 12mm, which is a great difference from the actual sheet thickness used, and thus it was understood that the inventors did not sufficiently recognize the influence of the rolling process on the mechanical properties of the materials. Thirdly, the heating schedule for testing the hydrogen induced cracking tensile sample is 900-950 ℃ for x30min, while the actually formed plate-shaped heating schedule is 900-950 ℃ for x5min, the difference between the two processes is great, the properties of the steel obtained by the method have great difference, and the obtained result is lack of persuasion.
Chinese patent publications CN110079743A and CN110157864A disclose two kinds of hot forming steel with low delayed cracking sensitivity, respectively, and both documents improve delayed cracking performance by adding micro alloy elements such as Nb and Ti into the steel to produce fine precipitated phases, and do not relate to the influence of inclusions in the cast steel on delayed cracking, and do not provide corresponding improvement measures and laws in the smelting process.
Disclosure of Invention
The invention aims to overcome the defects in the prior art and provides a steelmaking method capable of improving the delayed cracking resistance of the hot forming steel in CSP production line production so as to ensure that Al in the steel 2 O 3 The maximum size of the inclusion is reduced from about 20 mu m to not more than 10 mu m, the inclusion is changed from irregular inclusion to spherical inclusion, and the distribution density is changed from 4.63/mm 2 The temperature of the mixture is reduced to be not more than 0.8 piece/mm 2 The hydrogen-induced delayed cracking sensitivity of the steel is reduced to less than or equal to 50 percent from the original 80 percent.
The measures for realizing the aim are as follows:
a steel-making method capable of improving delayed cracking resistance of hot forming steel in CSP production line comprises the following production steps:
1) desulfurizing the molten iron, controlling S in the molten iron to be less than or equal to 0.002 percent, and controlling the exposed surface of the molten iron to be not less than 96 percent after slagging off;
2) conventionally smelting in an electric furnace or a converter, and controlling the smelting end point in molten steel: c: 0.05-0.06%, and less than or equal to 0.025% of T [ O ];
adding a deoxidizer for pre-deoxidation before tapping, and keeping blowing argon in the whole deoxidation alloying process;
3) performing LF refining, and performing soft blowing conventionally in the refining process, wherein the soft blowing time is 3-5 min, and the T [ O ] is controlled to be less than or equal to 0.0020%;
in the slag making, CaO/Al in the slag is controlled 2 O 3 1.6 to 2.0;
4) carrying out RH vacuum treatment with the vacuum degree not exceeding 150 Pa;
after RH vacuum treatment is finished, calcium line feeding treatment is carried out, and the calcium line amount is fed according to 0.15-0.40 kg per ton of steel;
carrying out soft argon blowing on the molten steel, wherein the soft argon blowing time is 5-10 min, the argon flow is controlled to be 30-50 Nl/min, and the molten steel is strictly forbidden to be exposed in the argon blowing process;
5) pouring into a blank, and controlling the superheat degree of the tundish molten steel to be 10-15 ℃ in the continuous casting process; the blank drawing speed is 4.0-6.0 m/min; the spherical impurities in the casting blank are made of CaS, MgO and (CaO) 12 (Al 2 O 3 ) 7 The particle diameter of the spherical inclusion is controlled to be less than or equal to 10 mu m;
6) heating the casting blank, wherein the heating temperature is controlled to be 1100-1200 ℃;
7) carrying out hot rolling, and controlling the final rolling temperature to be 830-910 ℃;
8) cooling the laminar flow to a coiling temperature, coiling, and controlling the coiling temperature to be 615-665 ℃;
9) carrying out conventional pickling and cold rolling to the thickness of a finished product, and controlling the total cold rolling reduction rate to be 55-65%;
10) then annealing the product, wherein the annealing temperature is controlled to be 780-840 ℃;
11) cutting and blanking a steel plate, then heating to austenitize the steel plate under the protection of nitrogen, wherein the austenitizing temperature is 850-910 ℃, and preserving heat for 4-6 min at the temperature;
12) and performing conventional quenching after hot stamping forming, and naturally cooling to room temperature.
Preferably: in the slag making, CaO/Al in the slag is controlled 2 O 3 Is between 1.7 and 1.93.
Preferably: the vacuum degree does not exceed 120 Pa.
Preferably: the particle diameter of the spherical inclusion is controlled to be less than or equal to 9.0 mu m.
Preferably: the blank drawing speed is 4.5-5.5 m/min.
Description of the drawings: the invention is suitable for the component composition and content with the tensile strength not lower than 1000 MPa.
Action and mechanism of the main process in the invention
The invention controls CaO/Al in slag in the slag-making 2 O 3 Preferably controlling CaO/Al in the slag within 1.6-2.0 2 O 3 1.7-1.93, because the alkalinity of the slag is small, more Al can be adsorbed 2 O 3 The sulfur capacity is increased by properly increasing the alkalinity of the slag, and the desulfurization capability is enhanced.
The vacuum degree is controlled not to exceed 150Pa, preferably not to exceed 120Pa in the RH vacuum treatment, because the high vacuum can effectively reduce the amount of impurities and improve the cleanliness of steel, but the vacuum time and energy consumption required by the overhigh vacuum degree are increased, the production rhythm is prolonged, the cost control is not facilitated, and the vacuum degree needs to be properly controlled.
The calcium wire feeding treatment is carried out after the RH vacuum treatment is finished, and the calcium wire feeding amount is controlled to be 0.15-0.40 kg/ton steel, because the calcium treatment is adopted after the RH, the inclusions can be modified, and Al is changed 2 O 3 The inclusion is transformed into the C12A7 inclusion with low melting point, and the shape of the inclusion is transformed from irregular shape to spherical shape, thereby greatly reducing the stress of the inclusion and the steel base and further reducing the delayed cracking sensitivity; the continuous casting of the thin slab is adopted in the continuous casting process, and the high-speed drawing of the slab is kept, so that the calcium aluminate inclusion aggregation and growth in the continuous casting process can be effectively prevented, the size of the inclusion is reduced, and the function of reducing the stress in steel can be realized. Compared with the prior art, the invention has the advantages that the size, the shape and the quantity of the inclusions are obviously changed, the maximum size is reduced from about 20 mu m to less than 10 mu m, the irregular inclusions are changed into the spherical inclusions, and the distribution density is changed from 4.63 inclusions/mm 2 Down to 0.8 pieces/mm 2 The hydrogen-induced delayed cracking sensitivity of the steel is reduced from 80% to less than or equal to 50%.
The invention controls the superheat degree of the tundish molten steel at 10-15 ℃, and controls the blank drawing speed at 4.0-6.0 m/min, because the low superheat degree is favorable for quick blank drawing, thereby controlling the inclusion growth in the steel.
The heating temperature of the casting blank is controlled to be 1100-1200 ℃, because the temperature is too low, the rolling resistance is large, the plate shape control is not facilitated, the obtained structure is not uniform, and the temperature is too high, so that the burning loss of the casting blank is large.
Compared with the prior art, the method has the advantages that the calcium dosage is 0.15-0.40 kg/ton steel, so that Al is added 2 O 3 The maximum size of the inclusion is reduced from about 20 mu m to not more than 10 mu m, the inclusion is changed from irregular inclusion into spherical inclusion, and the distribution density is changed from 4.63/mm 2 The temperature of the mixture is reduced to be not more than 0.8 piece/mm 2 The hydrogen-induced delayed cracking sensitivity of the steel is reduced to less than or equal to 50 percent from the original 80 percent.
Detailed Description
The present invention is described in detail below:
table 1 is a list of values of chemical components in various examples and comparative examples of the present invention under different strengths;
table 2 is a table of the main process parameters of each example of the present invention and comparative example;
table 3 is a list of the performance test cases of the examples and comparative examples of the present invention;
the examples of the invention were produced as follows
1) Desulfurizing molten iron, controlling S in the molten iron to be less than or equal to 0.002 percent, and controlling the exposed surface of the molten iron to be not less than 96 percent after slagging-off;
2) conventionally smelting in an electric furnace or a converter, and controlling the smelting end point in molten steel: c: 0.05-0.06%, T [ O ] is less than or equal to 0.025%; adding a deoxidizer for pre-deoxidation before tapping, and keeping blowing argon in the whole deoxidation alloying process;
3) performing LF refining, performing soft blowing conventionally in the refining process, wherein the soft blowing time is 3-5 min, and controlling the T [ O ]]Less than or equal to 0.0020 percent; in the slag making, CaO/Al in the slag is controlled 2 O 3 1.6 to 2.0;
4) carrying out RH vacuum treatment, wherein the vacuum degree is not more than 150 Pa;
after RH vacuum treatment is finished, calcium line feeding treatment is carried out, and the calcium line amount is fed according to 0.15-0.40 kg per ton of steel;
carrying out soft argon blowing on the molten steel, wherein the soft argon blowing time is 5-10 min, the argon flow is controlled to be 30-50 Nl/min, and the molten steel is strictly forbidden to be exposed in the argon blowing process;
5) pouring into a blank, and controlling the superheat degree of the tundish molten steel to be 10-15 ℃ in the continuous casting process; the blank drawing speed is 4.0-6.0 m/min; the spherical shaped sundries in the casting blank are made of CaS, MgO and (CaO) 12 (Al 2 O 3 ) 7 Are composed of and are sphericalThe particle diameter of the inclusion is controlled to be less than or equal to 10 mu m;
6) heating the casting blank, wherein the heating temperature is controlled to be 1100-1200 ℃;
7) carrying out hot rolling, and controlling the final rolling temperature to be 830-910 ℃;
8) cooling the laminar flow to a coiling temperature, coiling, and controlling the coiling temperature to be 615-665 ℃;
9) cold rolling to the thickness of a finished product after conventional pickling, and controlling the total rolling reduction rate of the cold rolling to be 55-65%;
10) then annealing the product, wherein the annealing temperature is controlled to be 780-840 ℃;
11) cutting and blanking a steel plate, then heating to austenitize the steel plate under the protection of nitrogen, wherein the austenitizing temperature is 850-910 ℃, and preserving heat for 4-6 min at the temperature;
12) and performing conventional quenching after hot stamping forming, and naturally cooling to room temperature.
TABLE 1 tabulation (wt%) of chemical composition values for various examples of the invention and comparative examples of the process at different strengths
TABLE 2 List of the main process parameters of the examples of the invention and the comparative examples
TABLE 2
The conventional mechanical properties of the test steel and the comparative steel are compared, and the results are shown in Table 3; meanwhile, the hydrogen-induced delayed cracking performance of the test steel and the comparative steel is compared, the hydrogen-induced delayed cracking performance is carried out in 0.2mol/L NaOH, the hydrogen charging current is dynamically applied, and the hydrogen charging current density is 0.5mA/cm 2 Tensile strain rate of 1.0X 10 -5 S, by calculating the extensionLoss of rate (hydrogen embrittlement index I) HE )
To evaluate the hydrogen-induced delayed cracking resistance, I ε Smaller values represent better resistance to hydrogen induced delayed cracking.
TABLE 3 Performance test results of inventive and comparative examples
As can be seen from the test results in Table 3, the examples have better performance, Al 2 O 3 The shape, size and quantity of inclusion are all obviously changed, and the hydrogen-induced delayed cracking sensitivity is reduced from the original 80% to less than or equal to 50%.
The present embodiments are merely preferred examples, and are not intended to limit the scope of the present invention.
Claims (5)
1. A steel-making method capable of improving delayed cracking resistance of hot forming steel in CSP production line comprises the following production steps:
1) desulfurizing molten iron, controlling S in the molten iron to be less than or equal to 0.002 percent, and controlling the exposed surface of the molten iron to be not less than 96 percent after slagging-off;
2) conventionally smelting in an electric furnace or a converter, and controlling the smelting end point in molten steel: c: 0.05-0.06%, and less than or equal to 0.025% of T [ O ]; adding a deoxidizer for pre-deoxidation before tapping, and keeping blowing argon in the whole deoxidation alloying process;
3) performing LF refining, performing soft blowing conventionally in the refining process, wherein the soft blowing time is 3-5 min, and controlling the T [ O ]]Less than or equal to 0.0020 percent; in the slag making, CaO/Al in the slag is controlled 2 O 3 1.6 to 2.0;
4) carrying out RH vacuum treatment for 10-15 min, wherein the vacuum degree is not more than 150 Pa;
after RH vacuum treatment is finished, calcium line feeding treatment is carried out, and the calcium line amount is fed according to 0.15-0.40 kg per ton of steel;
carrying out soft argon blowing on the molten steel, wherein the soft argon blowing time is 5-10 min, the argon flow is controlled to be 30-50 Nl/min, and the molten steel is strictly forbidden to be exposed in the argon blowing process;
5) pouring into a blank, and controlling the superheat degree of the tundish molten steel to be 10-15 ℃ in the continuous casting process; the blank drawing speed is 4.0-6.0 m/min; the spherical shaped sundries in the casting blank are made of CaS, MgO and (CaO) 12 (Al2O3) 7 The particle diameter of the spherical inclusion is controlled to be less than or equal to 10 mu m;
6) heating the casting blank, wherein the heating temperature is controlled to be 1100-1200 ℃;
7) carrying out hot rolling, and controlling the final rolling temperature to be 830-910 ℃;
8) cooling the laminar flow to a coiling temperature, coiling, and controlling the coiling temperature to be 615-665 ℃;
9) carrying out conventional pickling and cold rolling to the thickness of a finished product, and controlling the total cold rolling reduction rate to be 55-65%;
10) then annealing the product, wherein the annealing temperature is controlled to be 780-840 ℃;
11) cutting and blanking a steel plate, then heating to austenitize the steel plate under the protection of nitrogen, wherein the austenitizing temperature is 850-910 ℃, and preserving heat for 4-6 min at the temperature;
12) and performing conventional quenching after hot stamping forming, and naturally cooling to room temperature.
2. The steelmaking process as claimed in claim 1 for producing in a CSP line steel with improved resistance to delayed cracking of the hot formed steel, wherein: in the slag making, the CaO/Al content of the slag is controlled 2 O 3 Is between 1.7 and 1.93.
3. The steel making method for producing steel capable of improving the delayed cracking resistance of hot formed steel on the CSP production line as recited in claim 1 wherein: the vacuum degree does not exceed 120 Pa.
4. The steelmaking process as claimed in claim 1 for producing in a CSP line steel with improved resistance to delayed cracking of the hot formed steel, wherein: the particle diameter of the spherical inclusion is controlled to be less than or equal to 9.0 mu m.
5. The steelmaking process as claimed in claim 1 for producing in a CSP line steel with improved resistance to delayed cracking of the hot formed steel, wherein: the blank drawing speed is 4.5-5.5 m/min.
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