CN116254483B - High-strength steel plate with excellent low-temperature impact toughness and manufacturing method thereof - Google Patents
High-strength steel plate with excellent low-temperature impact toughness and manufacturing method thereof Download PDFInfo
- Publication number
- CN116254483B CN116254483B CN202310048924.8A CN202310048924A CN116254483B CN 116254483 B CN116254483 B CN 116254483B CN 202310048924 A CN202310048924 A CN 202310048924A CN 116254483 B CN116254483 B CN 116254483B
- Authority
- CN
- China
- Prior art keywords
- temperature
- equal
- refining
- controlled
- less
- 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.)
- Active
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 155
- 239000010959 steel Substances 0.000 title claims abstract description 155
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 27
- 238000010438 heat treatment Methods 0.000 claims abstract description 50
- 238000005096 rolling process Methods 0.000 claims abstract description 47
- 238000010791 quenching Methods 0.000 claims abstract description 26
- 230000000171 quenching effect Effects 0.000 claims abstract description 26
- 238000005496 tempering Methods 0.000 claims abstract description 20
- 238000010521 absorption reaction Methods 0.000 claims abstract description 19
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 19
- 229910052739 hydrogen Inorganic materials 0.000 claims abstract description 18
- 238000009749 continuous casting Methods 0.000 claims abstract description 16
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 16
- 238000001816 cooling Methods 0.000 claims abstract description 15
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 15
- 238000003723 Smelting Methods 0.000 claims abstract description 12
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 11
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 9
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 9
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 9
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 8
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 8
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 8
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 229910052729 chemical element Inorganic materials 0.000 claims abstract description 3
- 238000007670 refining Methods 0.000 claims description 80
- 239000002893 slag Substances 0.000 claims description 57
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 44
- 238000005266 casting Methods 0.000 claims description 40
- 238000010079 rubber tapping Methods 0.000 claims description 25
- 229910052786 argon Inorganic materials 0.000 claims description 22
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 12
- 238000007664 blowing Methods 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 9
- 238000009792 diffusion process Methods 0.000 claims description 8
- 239000005997 Calcium carbide Substances 0.000 claims description 7
- 235000008733 Citrus aurantifolia Nutrition 0.000 claims description 7
- 229910008455 Si—Ca Inorganic materials 0.000 claims description 7
- 235000011941 Tilia x europaea Nutrition 0.000 claims description 7
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 7
- 239000011575 calcium Substances 0.000 claims description 7
- 229910052799 carbon Inorganic materials 0.000 claims description 7
- 239000003795 chemical substances by application Substances 0.000 claims description 7
- 239000004571 lime Substances 0.000 claims description 7
- 238000002844 melting Methods 0.000 claims description 7
- 230000008018 melting Effects 0.000 claims description 7
- CLZWAWBPWVRRGI-UHFFFAOYSA-N tert-butyl 2-[2-[2-[2-[bis[2-[(2-methylpropan-2-yl)oxy]-2-oxoethyl]amino]-5-bromophenoxy]ethoxy]-4-methyl-n-[2-[(2-methylpropan-2-yl)oxy]-2-oxoethyl]anilino]acetate Chemical compound CC1=CC=C(N(CC(=O)OC(C)(C)C)CC(=O)OC(C)(C)C)C(OCCOC=2C(=CC=C(Br)C=2)N(CC(=O)OC(C)(C)C)CC(=O)OC(C)(C)C)=C1 CLZWAWBPWVRRGI-UHFFFAOYSA-N 0.000 claims description 7
- 238000010891 electric arc Methods 0.000 claims description 5
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 238000009628 steelmaking Methods 0.000 claims description 3
- 238000007689 inspection Methods 0.000 claims 1
- 238000004321 preservation Methods 0.000 abstract description 9
- 229910001566 austenite Inorganic materials 0.000 description 11
- 239000011651 chromium Substances 0.000 description 11
- 238000000034 method Methods 0.000 description 11
- 239000010936 titanium Substances 0.000 description 11
- 238000005728 strengthening Methods 0.000 description 9
- 238000007599 discharging Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 7
- 229910001563 bainite Inorganic materials 0.000 description 5
- 230000008569 process Effects 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 230000006870 function Effects 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- 230000009471 action Effects 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 229910052761 rare earth metal Inorganic materials 0.000 description 2
- 150000002910 rare earth metals Chemical class 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- FBPFZTCFMRRESA-JGWLITMVSA-N D-glucitol Chemical compound OC[C@H](O)[C@@H](O)[C@H](O)[C@H](O)CO FBPFZTCFMRRESA-JGWLITMVSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000004913 activation Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000001934 delay Effects 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000009845 electric arc furnace steelmaking Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000004886 process control Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- 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
- C21C7/0075—Treating in a ladle furnace, e.g. up-/reheating of molten steel within the ladle
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- 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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Mechanical Engineering (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses a high-strength steel plate with excellent low-temperature impact toughness and a manufacturing method thereof, wherein the steel contains ：C 0.11～0.15%,Si 0.2～0.3%,Mn 0.6～0.9%,Cr 0.8～1.2%,Mo 0.7～1.2%,Ni 0.1～0.3%,V 0.1～0.3%,Nb 0.01～0.03%,Ti 0.01～0.03%,Al 0.02～0.06%,RE≤0.01%,P≤0.015%,S≤0.005%,H≤0.0003%,N≤0.005%, mass percent of chemical elements and the balance of Fe and unavoidable impurities. The manufacturing method comprises the following steps: (1) smelting; (2) continuous casting; (3) heating: heating to 1050-1200 deg.c and maintaining for 1-3 hr; (4) rolling: the final rolling temperature is more than or equal to 850 ℃, and the steel is cooled to normal temperature after rolling; (4) quenching and tempering heat treatment: quenching at 900-980 deg.c for 40-80 min, austenitizing and water quenching; tempering temperature is 500-700 ℃, heat preservation is carried out for 60-120 min, and air cooling is carried out to room temperature. The yield strength Rp 0.2 of the steel plate produced by the invention is more than or equal to 1000MPa, the tensile strength Rm is more than or equal to 1150MPa, the elongation delta is more than or equal to 22wt percent, and the impact absorption work Akv at-40 ℃ is more than or equal to 210J.
Description
Technical Field
The invention relates to the technical field of high-strength steel manufacturing, in particular to a high-strength steel plate with excellent low-temperature impact toughness and a manufacturing method thereof.
Background
With the rapid development of industrial economy in China, the requirements on steel materials are more and more increased, and steel materials used in high-cold areas and at low temperature are subjected to severe environments such as low temperature, high strength and out-of-service conditions, so that the requirements on the performance of the steel materials, especially the low-temperature impact toughness, are higher, and the safety and the service performance of equipment or parts are met. At present, the steel has the phenomena of high strength and low toughness in the manufacturing process, and in order to improve the strength and toughness of the steel, a large amount of alloy elements are generally added into the steel through optimizing component design, or the strength and low-temperature toughness of the steel are improved through optimizing and precisely controlling the production process, so that the production cost is increased, and the quality of the product is unstable due to the difficulty in precisely controlling the process.
Therefore, a high-strength steel sheet having excellent low-temperature impact toughness and a method for manufacturing the same are urgently researched and developed so as to improve the low-temperature toughness of the steel sheet while ensuring the strength of the steel sheet at a low production cost.
Disclosure of Invention
The invention aims to provide a production method of a low-temperature impact toughness steel plate with stable production process and excellent performance, which ensures that the steel plate has high strength and good low-temperature toughness to meet the high standard requirement of customers through relevant process control.
In order to solve the technical problems, the technical scheme provided by the invention is as follows: a high-strength steel plate with excellent low-temperature impact toughness comprises the following chemical elements in percentage by mass of ： C 0.11～0.15%,Si 0.2～0.3%,Mn 0.6～0.9%,Cr 0.8～1.2%,Mo 0.7～1.2%,Ni 0.1～0.3%,V 0.1～0.3%,Nb 0.01~0.03%,Ti 0.01~0.03%,Al 0.02~0.06%,RE≤0.01%,P≤0.015%,S≤0.005%,H≤0.0003%,N≤0.005%, and the balance of iron and unavoidable impurity elements.
The reason for adopting the above composition design is as follows:
(1) C: c is an effective element for improving the strength of steel, but the increase of the carbon content reduces the toughness of steel plastic, and the application adopts lower carbon content, and combines with microalloying elements Nb, V and Ti to exert the fine crystal strengthening and precipitation strengthening effects. Therefore, in the high-strength steel with excellent impact toughness according to the present application, the mass percentage of the C element is controlled to be between 0.11 and 0.15%.
(2) Si: si has very obvious solid solution strengthening effect, can improve the strength and hardness of steel, improve the ductility and toughness of steel, reduce the ductile-brittle transition temperature of steel, and simultaneously, si can increase the activity of C in austenite, prevent cementite from separating out and improve the tempering resistance stability of steel. Therefore, in the high-strength steel with excellent impact toughness, the mass percentage of Si is controlled within the range of 0.2-0.3% in order to comprehensively improve the comprehensive mechanical properties of the high-strength steel.
(3) Mn: mn is dissolved in steel to have a solid solution strengthening effect, and Mn delays ferrite and pearlite transformation and lowers transformation temperature of bainite, which is beneficial to forming fine grain structure, but too high Mn content lowers toughness of steel. Therefore, in the high-strength steel with excellent impact toughness, in order to comprehensively improve the comprehensive mechanical properties of the high-strength steel, the mass percentage of Mn is controlled to be 0.6-0.9%.
(4) Cr: cr has the function of solid solution strengthening, improves the hardenability of steel, improves the strength and the hardness of the steel in a heat treatment state, and the addition of Cr not only promotes the transformation of bainite, but also changes the shape of bainite into a needle-like shape; meanwhile, as chromium is added, a finer bainitic ferrite structure is formed, and the yield strength, tensile strength and yield ratio of the steel are improved. In order to comprehensively improve the comprehensive mechanical properties of the high-strength steel, the mass percentage content of Cr is controlled within the range of 0.8-1.2%.
(5) Mo: mo is dissolved in ferrite, so that the self-diffusion activation energy of iron is increased, and the recovery and recrystallization temperature of steel is improved; mo can enable the C curve of steel to move right, so that the hardenability of the steel is remarkably improved, and meanwhile, the tempering stability of the steel is improved; mo can also improve the high-temperature brittleness of the alloy quenched and tempered steel and improve the toughness of tempered sorbite. In order to comprehensively improve the comprehensive mechanical properties of the high-strength steel, the mass percentage content of Mo is controlled within the range of 0.7-1.2%.
(6) Ni: ni is a stable austenite element for improving toughness of steel, and when Ni is added together with Cr, bainite transformation can be effectively promoted. In order to comprehensively improve the comprehensive mechanical properties of the high-strength steel, the mass percentage of Ni is controlled within the range of 0.1-0.3%.
(7) V: v improves the mechanical property of steel mainly through the second phase particle precipitation strengthening effect, plays a role in inhibiting austenite recrystallization and preventing austenite grain growth to a certain extent through a controlled rolling process, and plays roles in grain refinement and precipitation strengthening to a certain extent. In order to comprehensively improve the comprehensive mechanical properties of the high-strength steel, the mass percentage content of V is controlled within the range of 0.1-0.3%.
(8) Nb: nb can refine austenite grains, and effectively improves the strength and toughness of the steel. Nb inhibits recrystallization in the high-temperature deformation process of austenite, and a small amount of Nb is added into plain carbon steel due to solute dragging action of Nb atoms and pinning action of Nb (C, N) on grain boundaries, so that grain growth in the heating process can be effectively inhibited, and original austenite grains are refined. In order to comprehensively improve the comprehensive mechanical properties of the high-strength steel, the mass percentage of Nb is controlled within the range of 0.01-0.03 percent.
(9) Ti: ti is an important microalloying fine-grain element, nitrogen in steel is fixed by titanium through strong precipitation strengthening and a certain degree of grain refinement, and the solid solution nitrogen content in the steel can be reduced through the treatment of the micro Ti, so that the strengthening effect of Nb is indirectly improved; meanwhile, tiN can effectively prevent austenite grains from growing up in the heating process, and plays a role in refining the austenite grains. In order to comprehensively improve the comprehensive mechanical properties of the high-strength steel, the mass percentage of Ti is controlled within the range of 0.01-0.02%.
(10) Al: al plays a role in deoxidization, and is matched with N in steel to form fine AlN precipitates, so that the growth of austenite grains can be effectively inhibited, but too high AlN, al2O3 and other impurities can reduce the impact toughness and fatigue performance of the steel. In order to comprehensively improve the comprehensive mechanical properties of the high-strength steel, the mass percentage content of Al is controlled within the range of 0.02-0.06%.
(11) RE: RE can outline the comprehensive mechanical properties of high-strength steel in the steel, has the functions of purifying molten steel and modifying, has higher affinity with oxygen and sulfur in the molten steel, has the function of purifying the molten steel, and has the function of refining the structure in the solidification process of the steel. However, the high rare earth RE in the steel is easy to block the continuous casting nozzle, so that continuous casting cannot be carried out smoothly, and the mass percent of the rare earth RE is controlled within less than or equal to 0.01 percent in order to comprehensively improve the comprehensive mechanical property of the high-strength steel.
(12) P and S: p and S are used as harmful elements in steel, and have great damage effect on cold bending and welding performance of the steel; the invention starts from the reduction of production cost and the improvement of product quality, the P content is controlled to be less than or equal to 0.015 percent, the S content is controlled to be less than or equal to 0.005 percent, and the influence of phosphorus and sulfur on the cold bending and welding performance of high-strength steel is reduced.
(13) H: h is prone to hydrogen embrittlement in steel. In steel having a strength of 1000MPa or more, a hydrogen induced fracture phenomenon occurs. In order to comprehensively improve the comprehensive mechanical properties of the high-strength steel, the mass percentage of H is controlled within the range that H is less than or equal to 0.0003 percent.
(14) N: n can improve the strength, low-temperature toughness and weldability of steel in the steel, increase ageing sensitivity and easily form air holes in the steel. In order to comprehensively improve the comprehensive mechanical properties of the high-strength steel, the mass percentage of N is controlled to be less than or equal to 0.005 percent.
A method for manufacturing a high-strength steel plate with excellent low-temperature impact toughness specifically comprises the following steps:
1) Steelmaking in an electric arc furnace or converter: the tapping temperature is controlled to 1580-1620 ℃, and the carbon end point is controlled to be
0.10%~0.14%，P≤0.015%，S≤0.01%；
2) LF+VD refining: the tapping temperature is controlled to 1560-1580 ℃, and the final carbon is controlled to be
0.10%~0.15%，P≤0.015%，S≤0.005%，H≤0.0003%，N≤0.005%；
3) Continuous casting: the molten steel is continuously cast into casting blanks with the thickness of 70-240 mm;
4) Heating: controlling the heating temperature of a casting blank at 1050-1200 ℃, and preserving heat for 1-3 hours;
5) Rolling: the casting blank is rolled by two sections, the first section is rolled on a roughing mill, and the initial rolling temperature is not less than 1050 ℃; the second section is finished on a finishing mill, the initial rolling temperature is 930-960 ℃, the final rolling temperature is more than or equal to 850 ℃, the thickness of the rolled steel plate is controlled to be 3-10 mm, and the rolled steel plate is cooled to room temperature;
6) Quenching and tempering heat treatment: the quenching temperature of the steel plate is 900-980 ℃, the temperature is kept for 40-80 min, and water quenching is carried out after austenitizing; the tempering temperature is 500-700 ℃, the temperature is kept for 60-120 min, and the air cooling is carried out to the room temperature.
As a preferable scheme, the electric arc furnace or the converter in the step 1) is forbidden to remove slag when tapping, and if slag is removed, the slag must be turned over or the slag must be refined after being turned over, so that the rephosphorization is prevented.
As a preferable scheme, in the step 2), the LF smelting time is controlled to be 40-100 min; lime, calcium carbide, a slag melting agent and premelting slag are added according to the condition of [ S ] in slag and molten steel during refining, the temperature is controlled to 1580-1600 ℃, and the quaternary basicity of slag is controlled to be about 2.0; during refining, carbon powder and aluminum powder are used for diffusion deoxidation; carrying out final deoxidation on molten steel after refining, feeding 0.8kg of Si-Ca wire into ton steel in a ladle, and controlling the flow rate of bottom blowing argon to be 40-60 NL/min; soft blowing for 6-10 min after Ca treatment; s is ensured to be less than or equal to 0.004% when the LF refining station is discharged;
The VD refining temperature is controlled to 1560-1620 ℃, the vacuum degree is 60-70 Pa, the refining time is 10-20 min, the argon flow is initially set to 30NL/min, the argon flow is increased by 10NL/min every two minutes, and the maximum is 120NL/min, and the refining temperature can be adjusted according to the slag quantity; after vacuum refining in a VD furnace, the composition requirements of the final molten steel are as follows: s is less than or equal to 0.005%, H is less than or equal to 0.0003%, and N is less than or equal to 0.005%.
As a preferable mode, the casting blank obtained in the step 3) is cooled to a normal temperature, and then the surface quality of the casting blank is checked, and the heating step described in the step 4) may be performed.
Compared with the prior art, the invention has the advantages that:
1. The thickness of the steel plate is 3-10 mm;
2. In order to reduce the production cost in the steel plate production, lower alloy content is adopted;
3. The quenching and tempering process is adopted, so that the steel plate is ensured to be in a martensite, bainite and retained austenite structure, and the steel plate is promoted to have high strength and excellent low-temperature toughness;
4. The manufacturing method is simple in production and reasonable in process design, and the obtained high-strength steel is high in strength and has excellent properties such as impact toughness and elongation. The yield strength Rp0.2 is more than or equal to 1000MPa, the tensile strength Rm is more than or equal to 1150MPa, the elongation delta is more than or equal to 22wt%, the impact absorption power Akv at 0 ℃ is more than or equal to 300J, the impact absorption power Akv at-20 ℃ is more than or equal to 250J, and the impact absorption power Akv at-40 ℃ is more than or equal to 210J.
Detailed Description
The following detailed description of examples is illustrative of the principles of the present application but is not intended to limit the scope of the application, i.e., a high strength steel sheet having excellent low temperature impact toughness and a method of manufacturing the same are not limited to the described examples.
A first embodiment of the present application provides a high-strength steel sheet having excellent low-temperature impact toughness, comprising the following components ：C 0.11～0.15%,Si 0.2～0.3%,Mn 0.6～0.9%,Cr 0.8～1.2%,Mo 0.7～1.2%,Ni 0.1～0.3%,V 0.1～0.3%,Nb 0.01~0.03%,Ti 0.01~0.03%,Al 0.02~0.06%,RE≤0.01%,P≤0.015%,S≤0.015%,H≤0.0003%,N≤0.005%, by weight percent, the balance being iron and unavoidable impurity elements.
The steel plate production method comprises the following steps:
S1, steelmaking by an electric arc furnace;
S2 LF+VD refining;
S3, continuous casting;
S4, heating;
s5, rolling;
S6, quenching and tempering heat treatment.
The production method of the high-strength steel plate with excellent low-temperature toughness specifically comprises the following steps:
(1) Step S1, electric arc furnace steelmaking: specifically, tapping C is controlled to be 0.11% -0.14%, P is controlled to be less than or equal to 0.015%, tapping temperature is controlled to be 1580-1620 ℃, slag discharging is forbidden during tapping, and if slag discharging occurs, slag turning or ladle pouring and refining are required to be performed, so that rephosphorization is prevented.
(2) Step S2 LF+VD refining: specifically, the LF smelting time is controlled to be 40-100 min; lime, calcium carbide, a slag melting agent and premelting slag are added according to the condition of [ S ] in slag and molten steel during refining, the temperature is controlled to 1580-1600 ℃, and the quaternary basicity of slag is controlled to be about 2.0; during refining, carbon powder and aluminum powder are used for diffusion deoxidation; after refining, carrying out final deoxidation on molten steel, feeding 0.8kg of Si-Ca wire per ton of steel into a ladle, and controlling the flow rate of bottom blowing argon to be 40-60 NL/min; soft blowing for 6-10 min after Ca treatment; ensure that S is less than or equal to 0.005 percent when the steel is discharged from the LF refining station. The VD refining temperature is controlled to 1560-1620 ℃, the vacuum degree is 60-70 Pa, the refining time is 10-20 min, the argon flow is initially set to 30NL/min, the argon flow is increased by 10NL/min every two minutes, and the maximum is 120NL/min, and the refining temperature can be adjusted according to the slag quantity. After vacuum refining in a VD furnace, the composition requirements of the final molten steel are as follows: s is less than or equal to 0.005%, H is less than or equal to 0.0003%, and N is less than or equal to 0.005%.
(3) Step S3, continuous casting: in the embodiment of the application, the molten steel obtained in the step S2 is subjected to continuous casting to obtain a casting blank, and the thickness of the casting blank is 70-240 mm.
(4) Step S4, heating: in the embodiment of the application, the casting blank obtained in the step S3 is cooled to normal temperature, the surface quality of the casting blank is checked, and then the casting blank is sent into a heating furnace for heating, the heating temperature is controlled to be 1050-1200 ℃, and the temperature is kept for 1-3 hours.
(5) Step S5, rolling: in the embodiment of the application, the heated casting blank obtained in the step S4 is rolled, two-section rolling is adopted, the first section is rolled on a roughing mill, and the initial rolling temperature is not less than 1050 ℃; the second section is finished on a finishing mill, the initial rolling temperature is 930-960 ℃, the final rolling temperature is more than or equal to 850 ℃, the thickness of the rolled steel plate is controlled to be 3-10 mm, and the rolled steel plate is cooled to room temperature.
(6) Step S6, heat treatment: in the embodiment of the application, the rolled plate obtained in the step S5 is subjected to heat treatment of quenching and tempering, the quenching temperature is 900-980 ℃, the heat preservation is carried out for 40-80 min, and water quenching is carried out after austenitizing; the tempering temperature is 500-700 ℃, the temperature is kept for 60-120 min, and the air cooling is carried out to the room temperature.
The invention is further described below with reference to examples.
Example 1
The high-strength steel composition with excellent impact toughness provided in this example comprises the following components in wt%:
C：0.12％;Si：0.24％;Mn：0.75％;Cr 0.84%,Mo 0.92%,Ni 0.16%,V 0.18%,Nb 0.03%,Ti 0.01%,Al 0.03%,RE≤0.01%,P≤0.015%,S≤0.005%,H≤0.0003%,N≤0.005%, The balance of Fe and unavoidable impurities.
The method for manufacturing the high-strength steel plate with excellent low-temperature impact toughness provided by the embodiment is as follows:
(1) Smelting in an arc furnace: the tapping C is controlled to be 0.125%, the tapping P is controlled to be less than or equal to 0.015%, the tapping temperature is 1580-1620 ℃, slag discharging is forbidden during tapping, and if slag is discharged, slag turning or ladle pouring and refining are required to be carried out, so that rephosphorization is prevented.
(2) LF+VD refining. LF refining: the smelting time is controlled to be 40-100 min, lime, calcium carbide, a slag melting agent and premelting slag are added according to the condition of [ S ] in slag and molten steel during refining, the temperature is controlled to be 1580-1600 ℃, and the quaternary basicity of slag is controlled to be about 2.0; during refining, carbon powder and aluminum powder are used for diffusion deoxidation; after refining, carrying out final deoxidation on molten steel, feeding 0.8kg of Si-Ca wire per ton of steel into a ladle, and controlling the argon flow to be 40-60 NL/min; soft blowing for 6-10 min after Ca treatment; ensure that S is less than or equal to 0.015 percent when the steel is discharged from the LF refining station. The VD refining temperature is controlled to 1560-1620 ℃, the vacuum degree is 60-70 Pa, the refining time is 10-20 min, the argon flow is initially set to 30NL/min, the argon flow is increased by 10NL/min every two minutes, and the maximum is 120NL/min, and the refining temperature can be adjusted according to the slag quantity. After vacuum refining in a VD furnace, the composition requirements of the final molten steel are as follows: s is less than or equal to 0.015 percent, H is less than or equal to 0.0003 percent, and N is less than or equal to 0.005 percent.
(3) Continuous casting: and carrying out continuous casting on the molten steel obtained by the VD refining to obtain a casting blank, wherein the thickness of the casting blank is 70mm.
(4) Heating: and cooling the obtained casting blank to normal temperature, then, checking the surface quality of the casting blank after cooling to normal temperature, and sending the casting blank into a heating furnace for heating, wherein the heating temperature is controlled to be 1100 ℃, and the temperature is kept for 1.5h.
(5) Rolling: rolling the casting blank obtained by heating in the step (4), wherein two sections of rolling are adopted, the first section of rolling is carried out on a roughing mill, and the initial rolling temperature is 1060 ℃; the second section is finished on a finishing mill, the initial rolling temperature is 940 ℃, the final rolling temperature is 860 ℃, the thickness obtained by rolling is controlled to be 3mm, and the rolled steel is cooled to room temperature.
(6) And (3) heat treatment: performing heat treatment of quenching and tempering on the rolled plate obtained in the step (5), wherein the quenching temperature is 930 ℃, the heat preservation is performed for 40min, and water quenching is performed after austenitizing; tempering temperature is 500 ℃, heat preservation is carried out for 40min, and air cooling is carried out to room temperature.
The mechanical properties of the produced high-strength steel plate with excellent low-temperature impact toughness are as follows: the yield strength rp 0.2=1140 MPa, the tensile strength rm=1280 MPa, the elongation δ=24wt%, the impact absorption work akv=330J at 0 ℃, the impact absorption work akv=270J at-20 ℃, and the impact absorption work akv=230J at-40 ℃.
Example 2
The chemical components of the high-strength steel plate with excellent low-temperature impact toughness provided by the embodiment are as follows in weight percent:
C：0.13％;Si：0.26％;Mn：0.82％;Cr 0.95 %,Mo 0.74%,Ni 0.25%,V 0.22%,Nb 0.02%,Ti 0.02%,Al 0.04%,RE≤0.01%,P≤0.015%,S≤0.015%,H≤0.0003%,N≤0.005%, The balance of Fe and unavoidable impurities.
The method for manufacturing the high-strength steel plate with excellent low-temperature impact toughness provided by the embodiment is as follows:
(1) Smelting in an arc furnace: the tapping C is controlled to be 0.128%, the tapping P is controlled to be less than or equal to 0.015%, the tapping temperature is 1580-1620 ℃, slag discharging is forbidden during tapping, and if slag discharging occurs, slag turning or ladle pouring and refining are required to be performed, so that rephosphorization is prevented.
(2) LF+VD refining. LF refining: the smelting time is controlled to be 40-100 min, lime, calcium carbide, a slag melting agent and premelting slag are added according to the condition of [ S ] in slag and molten steel during refining, the temperature is controlled to be 1580-1600 ℃, and the quaternary basicity of slag is controlled to be about 2.0; during refining, carbon powder and aluminum powder are used for diffusion deoxidation; after refining, carrying out final deoxidation on molten steel, feeding 0.8kg of Si-Ca wire per ton of steel into a ladle, and controlling the argon flow to be 40-60 NL/min; soft blowing for 6-10 min after Ca treatment; ensure that S is less than or equal to 0.005 percent when the steel is discharged from the LF refining station. The VD refining temperature is controlled to 1560-1620 ℃, the vacuum degree is 60-70 Pa, the refining time is 10-20 min, the argon flow is initially set to 30NL/min, the argon flow is increased by 10NL/min every two minutes, and the maximum is 120NL/min, and the refining temperature can be adjusted according to the slag quantity. After vacuum refining in a VD furnace, the composition requirements of the final molten steel are as follows: s is less than or equal to 0.005%, H is less than or equal to 0.0003%, and N is less than or equal to 0.005%.
(3) Continuous casting: and carrying out continuous casting on the molten steel obtained by the VD vacuum refining to obtain a casting blank, wherein the thickness of the casting blank is 100mm.
(4) Heating: and (3) cooling the casting blank obtained in the step (3) to normal temperature, checking the surface quality of the casting blank, and then sending the casting blank into a heating furnace for heating, controlling the heating temperature to 1120 ℃, and preserving the heat for 1.8h.
(5) Rolling: rolling the casting blank obtained by heating in the step (4), wherein two sections of rolling are adopted, the first section of rolling is carried out on a roughing mill, and the initial rolling temperature is 1070 ℃; the second section is finished on a finishing mill, the initial rolling temperature is 945 ℃, the final rolling temperature is 870 ℃, the thickness of the rolled steel plate is controlled to be 5mm, and the rolled steel plate is cooled to room temperature by water.
(6) And (3) heat treatment: performing heat treatment of quenching and tempering on the rolled plate obtained in the step (5), wherein the quenching temperature is 940 ℃, the heat preservation is performed for 50min, and water quenching is performed after austenitizing; the tempering temperature is 600 ℃, the temperature is kept for 50min, and the air cooling is carried out to the room temperature.
The mechanical properties of the produced high-strength steel plate with excellent low-temperature impact toughness are as follows: the yield strength rp 0.2=1080 MPa, the tensile strength rm=1210 MPa, the elongation δ=22wt%, the impact absorption work at 0 ℃ akv=320J, -the impact absorption work at 20 ℃ akv=260J, -the impact absorption work at 40 ℃ akv=220J.
Example 3
The chemical components of the high-strength steel sheet with excellent low-temperature impact toughness provided in this example are ：C：0.14％;Si：0.28％;Mn：0.88％;Cr 0.1.12%,Mo 1.05 %,Ni 0.18%,V 0.14%,Nb 0.02%,Ti 0.01%,Al 0.03%,RE≤0.01%,P≤0.015%,S≤0.005%,H≤0.0003%,N≤0.005%, as follows in wt% with the balance being Fe and unavoidable impurities.
The method for manufacturing the high-strength steel plate with excellent low-temperature impact toughness provided by the embodiment is as follows:
(1) Smelting in an arc furnace: the tapping C is controlled to be 0.142%, the tapping P is controlled to be less than or equal to 0.015%, the tapping temperature is 1580-1620 ℃, slag discharging is forbidden during tapping, and if slag is discharged, slag turning or ladle pouring and refining are required to be carried out, so that rephosphorization is prevented.
(2) LF+VD refining. LF refining: the smelting time is controlled to be 40-100 min, lime, calcium carbide, a slag melting agent and premelting slag are added according to the condition of [ S ] in slag and molten steel during refining, the temperature is controlled to be 1580-1600 ℃, and the quaternary basicity of slag is controlled to be about 2.0; during refining, carbon powder and aluminum powder are used for diffusion deoxidation; after refining, carrying out final deoxidation on molten steel, feeding 0.8kg of Si-Ca wire per ton of steel into a ladle, and controlling the argon flow to be 40-60 NL/min; soft blowing for 6-10 min after Ca treatment; ensure that S is less than or equal to 0.005 percent when the steel is discharged from the LF refining station. The VD refining temperature is controlled to 1560-1620 ℃, the vacuum degree is 60-70 Pa, the refining time is 10-20 min, the argon flow is initially set to 30NL/min, the argon flow is increased by 10NL/min every two minutes, and the maximum is 120NL/min, and the refining temperature can be adjusted according to the slag quantity. After vacuum refining in a VD furnace, the composition requirements of the final molten steel are as follows: s is less than or equal to 0.005%, H is less than or equal to 0.0003%, and N is less than or equal to 0.005%.
(3) Continuous casting: and carrying out continuous casting on the molten steel obtained by the VD vacuum refining to obtain a casting blank, wherein the thickness of the casting blank is 120mm.
(4) Heating: and (3) cooling the casting blank obtained in the step (3) to normal temperature, checking the surface quality of the casting blank, feeding the casting blank into a heating furnace for heating, controlling the heating temperature to 1150 ℃, and preserving heat for 2.2 hours.
(5) Rolling: rolling the casting blank obtained by heating in the step (4), wherein two sections of rolling are adopted, the first section of rolling is carried out on a roughing mill, and the initial rolling temperature is 1080 ℃; the second section is finished on a finishing mill, the initial rolling temperature is 950 ℃, the final rolling temperature is 880 ℃, the thickness of the rolled steel plate is controlled to be 7mm, and the rolled steel plate is cooled to room temperature by water.
(6) And (3) heat treatment: performing heat treatment of quenching and tempering on the rolled plate obtained in the step (5), and performing water quenching after austenitizing at the quenching temperature of 950 ℃ and the heat preservation time of 70 min; tempering temperature is 650 ℃, heat preservation is carried out for 70min, and air cooling is carried out to room temperature.
The mechanical properties of the produced high-strength steel plate with excellent low-temperature impact toughness are as follows: the yield strength Rp0.2=1120 MPa, the tensile strength Rm=1210 MPa, the elongation delta=22wt%, the impact absorption work at 0 ℃ Akv=320J, the impact absorption work at 20 ℃ Akv=260J and the impact absorption work at 40 ℃ Akv=220J.
Example 4
The chemical components of the high-strength steel sheet with excellent low-temperature impact toughness provided in this example are ：C：0.15％;Si：0.26％;Mn：0.65％;Cr 1.05%,Mo 1.14 %,Ni 0.23%,V 0.25%,Nb 0.01%,Ti 0.02%,Al 0.05%,RE≤0.01%,P≤0.015%,S≤0.005%,H≤0.0003%,N≤0.005%, as follows in wt% with the balance being Fe and unavoidable impurities.
The method for manufacturing the high-strength steel plate with excellent low-temperature impact toughness provided by the embodiment is as follows:
(1) Smelting in an arc furnace: the tapping C is controlled to be 0.145%, the tapping P is controlled to be less than or equal to 0.015%, the tapping temperature is 1580-1620 ℃, slag discharging is forbidden during tapping, and if slag is discharged, slag turning or ladle pouring and refining are required to be carried out, so that rephosphorization is prevented.
(2) LF+VD refining. LF refining: the smelting time is controlled to be 40-100 min, lime, calcium carbide, a slag melting agent and premelting slag are added according to slag and [ S ] during refining, the temperature is controlled to be 1580-1600 ℃, and the quaternary basicity of slag is controlled to be about 2.0; during refining, carbon powder and aluminum powder are used for diffusion deoxidation; after refining, carrying out final deoxidation, feeding 0.8kg of Si-Ca wire per ton of steel into the ladle, and controlling the argon flow to be 40-60 NL/min; soft blowing for 6-10 min after Ca treatment; ensure that S is less than or equal to 0.005 percent when the steel is discharged from the LF refining station. The VD refining temperature is controlled to 1560-1620 ℃, the vacuum degree is 60-70 Pa, the refining time is 10-20 min, the argon flow is initially set to 30NL/min, the argon flow is increased by 10NL/min every two minutes, and the maximum is 120NL/min, and the refining temperature can be adjusted according to the slag quantity. After vacuum refining in a VD furnace, the composition requirements of the final molten steel are as follows: s is less than or equal to 0.005%, H is less than or equal to 0.0003%, and N is less than or equal to 0.005%.
(3) Continuous casting: and carrying out continuous casting on the molten steel obtained by the VD vacuum refining to obtain a casting blank, wherein the thickness of the casting blank is 200mm.
(4) Heating: and (3) cooling the casting blank obtained in the step (3) to normal temperature, checking the surface quality of the casting blank, feeding the casting blank into a heating furnace for heating, controlling the heating temperature to 1200 ℃, and preserving the heat for 2.5 hours.
(5) Rolling: rolling the casting blank obtained by heating in the step (4), wherein two sections of rolling are adopted, the first section of rolling is carried out on a roughing mill, and the initial rolling temperature is 1100 ℃; the second section is finished on a finishing mill, the initial rolling temperature is 960 ℃, the final rolling temperature is 890 ℃, the thickness of the rolled steel plate is controlled to be 10mm, and the rolled steel plate is cooled to room temperature by water.
(6) And (3) heat treatment: performing heat treatment of quenching and tempering on the rolled plate obtained in the step (5), wherein the quenching temperature is 960 ℃, the heat preservation is performed for 80 minutes, and water quenching is performed after austenitizing; tempering temperature is 700 ℃, heat preservation is carried out for 80min, and air cooling is carried out to room temperature.
The mechanical properties of the produced high-strength steel plate with excellent low-temperature impact toughness are as follows: the yield strength rp 0.2=1145 MPa, the tensile strength rm=1234 MPa, the elongation δ=22.5 wt%, the impact absorption work at 0 ℃ akv=323J, -the impact absorption work at 20 ℃ akv=264J, -the impact absorption work at 40 ℃ akv=225J.
It should be noted that the combination of the technical features in the present invention is not limited to the combination described in the claims or the combination described in the specific embodiments, and all the technical features described in the present invention may be freely combined or combined in any manner unless contradiction occurs between them.
It should also be noted that the above-recited embodiments are merely specific examples of the present invention. It is apparent that the present invention is not limited to the above embodiments, and similar changes or modifications will be apparent to those skilled in the art from the present disclosure, and it is intended to be within the scope of the present invention.
Claims (4)
1. A high-strength steel plate with excellent low-temperature impact toughness is characterized in that the steel contains chemical elements and the balance of ： C 0.11～0.15%,Si 0.2～0.3%,Mn 0.6～0.9%,Cr 0.8～1.2%,Mo 0.7～1.2%,Ni 0.1～0.3%,V 0.1～0.3%,Nb 0.01~0.03%,Ti 0.01~0.03%,Al 0.02~0.06%,RE≤0.01%,P≤0.015%,S≤0.005%,H≤0.0003%,N≤0.005%, mass percent of iron and unavoidable impurity elements;
The manufacturing method of the high-strength steel plate specifically comprises the following steps:
1) Steelmaking in an electric arc furnace or converter: the tapping temperature is controlled to 1580-1620 ℃, the carbon end point is controlled to be 0.10-0.14%, P is less than or equal to 0.015%, and S is less than or equal to 0.01%;
2) LF+VD refining: the tapping temperature is controlled to 1560-1580 ℃, the carbon at the end point is controlled to be 0.10% -0.15%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, H is less than or equal to 0.0003%, and N is less than or equal to 0.005%;
3) Continuous casting: the molten steel is continuously cast into casting blanks with the thickness of 70-240 mm;
4) Heating: controlling the heating temperature of a casting blank at 1050-1200 ℃, and preserving heat for 1-3 hours;
5) Rolling: the casting blank is rolled by two sections, the first section is rolled on a roughing mill, and the initial rolling temperature is not less than 1050 ℃; the second section is finished on a finishing mill, the initial rolling temperature is 930-960 ℃, the final rolling temperature is more than or equal to 850 ℃, the thickness of the rolled steel plate is controlled to be 3-10 mm, and the rolled steel plate is cooled to room temperature;
6) Quenching and tempering heat treatment: the quenching temperature of the steel plate is 900-980 ℃, the temperature is kept for 40-80 min, and water quenching is carried out after austenitizing; the tempering temperature is 500-700 ℃, the temperature is kept for 60-120 min, and the air cooling is carried out to the room temperature;
The yield strength Rp0.2 of the high-strength steel plate is more than or equal to 1000MPa, the tensile strength Rm is more than or equal to 1150MPa, the elongation delta is more than or equal to 22wt%, the impact absorption work Akv at 0 ℃ is more than or equal to 300J, the impact absorption work Akv at-20 ℃ is more than or equal to 250J, and the impact absorption work Akv at-40 ℃ is more than or equal to 210J.
2. A high-strength steel sheet having excellent low-temperature impact toughness according to claim 1, wherein: and (3) the electric arc furnace or the converter in the step 1) is forbidden to remove slag when tapping, and if slag is removed, slag turning or ladle-down and refining are required to be carried out, so that rephosphorization is prevented.
3. A high-strength steel sheet having excellent low-temperature impact toughness according to claim 1, wherein: the LF smelting time in the step 2) is controlled to be 40-100 min; lime, calcium carbide, a slag melting agent and premelted refining slag are added according to the condition of [ S ] in slag and molten steel during refining, the temperature is controlled to 1580-1600 ℃, and the quaternary basicity of the slag is controlled to 2.0; during refining, carbon powder and aluminum powder are used for diffusion deoxidation; after refining, final deoxidization is carried out, 0.8kg of Si-Ca line is fed into ton steel in the ladle, and simultaneously, the flow rate of bottom blowing argon is controlled to be 40-60 NL/min; soft blowing for 6-10 min after Ca treatment; s is ensured to be less than or equal to 0.004% when the LF refining station is discharged;
Controlling the VD refining temperature to 1560-1620 ℃, controlling the vacuum degree to be 60-70 Pa, controlling the refining time to be 10-20 min, setting the argon flow to be 30NL/min, increasing the argon flow by 10NL/min every two minutes, and adjusting the maximum argon flow according to the slag quantity; after vacuum refining in a VD furnace, the composition requirements of the final molten steel are as follows: s is less than or equal to 0.005%, H is less than or equal to 0.0003%, and N is less than or equal to 0.005%.
4. A high-strength steel sheet having excellent low-temperature impact toughness according to claim 1, wherein: and (3) cooling the casting blank obtained in the step (3), cooling to normal temperature, and performing surface quality inspection on the casting blank, wherein the heating step in the step (4) can be performed.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202310048924.8A CN116254483B (en) | 2023-02-01 | 2023-02-01 | High-strength steel plate with excellent low-temperature impact toughness and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202310048924.8A CN116254483B (en) | 2023-02-01 | 2023-02-01 | High-strength steel plate with excellent low-temperature impact toughness and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN116254483A CN116254483A (en) | 2023-06-13 |
| CN116254483B true CN116254483B (en) | 2024-06-14 |
Family
ID=86683661
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202310048924.8A Active CN116254483B (en) | 2023-02-01 | 2023-02-01 | High-strength steel plate with excellent low-temperature impact toughness and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN116254483B (en) |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102224268A (en) * | 2008-11-26 | 2011-10-19 | 住友金属工业株式会社 | Seamless steel pipe and method for manufacturing same |
| CN103097556A (en) * | 2010-06-07 | 2013-05-08 | 罗奇钢铁公司 | Method for producing a hot-rolled steel product, and a hot-rolled steel |
Family Cites Families (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0737648B2 (en) * | 1991-03-22 | 1995-04-26 | 新日本製鐵株式会社 | Manufacturing method of fire-resistant steel plate for construction with excellent toughness |
| JPH08143955A (en) * | 1994-11-18 | 1996-06-04 | Nippon Steel Corp | Production of thick-walled high tensile strength steel uniformized in strength in plate thickness direction |
| AU2013319622B2 (en) * | 2012-09-19 | 2016-10-13 | Jfe Steel Corporation | Wear-resistant steel plate having excellent low-temperature toughness and corrosion wear resistance |
| CN103147017A (en) * | 2013-03-21 | 2013-06-12 | 宝山钢铁股份有限公司 | Steel plate with high strength and excellent low-temperature toughness and manufacturing method thereof |
| CN104480406A (en) * | 2014-11-28 | 2015-04-01 | 宝山钢铁股份有限公司 | Low-alloy high-strength high-toughness steel plate and manufacturing method thereof |
| CN111441000A (en) * | 2020-03-30 | 2020-07-24 | 江阴兴澄特种钢铁有限公司 | 690 MPa-yield-strength low-yield-ratio high-strength steel plate and manufacturing method thereof |
| CN112048675A (en) * | 2020-07-30 | 2020-12-08 | 江阴兴澄特种钢铁有限公司 | Low-yield-ratio granular bainite high-strength steel plate used in low-temperature environment and manufacturing method thereof |
-
2023
- 2023-02-01 CN CN202310048924.8A patent/CN116254483B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102224268A (en) * | 2008-11-26 | 2011-10-19 | 住友金属工业株式会社 | Seamless steel pipe and method for manufacturing same |
| CN103097556A (en) * | 2010-06-07 | 2013-05-08 | 罗奇钢铁公司 | Method for producing a hot-rolled steel product, and a hot-rolled steel |
Also Published As
| Publication number | Publication date |
|---|---|
| CN116254483A (en) | 2023-06-13 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN110541117B (en) | 620 MPa-grade high-performance bridge steel welded at low preheating temperature and preparation method thereof | |
| CN111441000A (en) | 690 MPa-yield-strength low-yield-ratio high-strength steel plate and manufacturing method thereof | |
| CN111455278A (en) | Thick hot-rolled high-strength steel plate coil with excellent low-temperature toughness and for 800MPa cold forming and manufacturing method thereof | |
| CN114134430B (en) | High-hardenability 35SiMnCrMoB steel for wear-resistant parts of engineering machinery and manufacturing method thereof | |
| CN109161671B (en) | High-strength EH36 steel plate for high heat input welding and manufacturing method thereof | |
| CN103882330A (en) | Low-yield-ratio ultrahigh-strength non-quenched and tempered steel plate and production method thereof | |
| CN110629114A (en) | Low-cost high-strength high-toughness bridge steel and preparation method thereof | |
| CN112813344B (en) | High-strength high-toughness easy-to-weld structural steel plate with yield strength of 620MPa and preparation method thereof | |
| CN108070789A (en) | The special thick steel of not less than 480MPa grades Ultra-fine Graineds of yield strength and preparation method | |
| KR20030021965A (en) | a hot-rolled steel sheet wiht good ultra low temperature toughness and the method of the same | |
| CN114107822B (en) | 15.9-grade high-strength bolt steel and production method and heat treatment method thereof | |
| CN115418553A (en) | High-corrosion-resistance weathering steel and preparation method thereof | |
| CN109797342B (en) | High-strength, high-toughness and atmospheric corrosion-resistant steel plate for manufacturing steel structure and manufacturing method thereof | |
| CN102337458B (en) | Steel with tensile strength not lower than 1100MPa for engineering machinery and production method thereof | |
| CN113604736B (en) | High-strength medium plate with yield strength of 800MPa and preparation method thereof | |
| CN116590611A (en) | High-strength ductile bridge steel plate and manufacturing method thereof | |
| CN114134387B (en) | 1300 MPa-tensile-strength thick-specification ultrahigh-strength steel plate and manufacturing method thereof | |
| CN116254483B (en) | High-strength steel plate with excellent low-temperature impact toughness and manufacturing method thereof | |
| CN115572901A (en) | 630 MPa-grade high-hardening-tempering-stability low-carbon low-alloy steel plate and manufacturing method thereof | |
| CN110747390B (en) | High-strength corrosion-resistant steel for ships and preparation method thereof | |
| CN111500938A (en) | Channel steel with yield strength of 420MPa for bridge and production method | |
| CN111235487A (en) | Steel for long-life drill rod and production method thereof | |
| CN115679221B (en) | Preparation method of drill steel | |
| CN110144517B (en) | High-strength high-toughness high-aluminum nickel-free easily-welded 40-70 mm-thick wear-resistant steel plate and preparation method thereof | |
| CN114737136B (en) | Production method of high-strength high-toughness hot continuous rolling thin steel plate with Brinell hardness of 400HBW |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |