CN116926427A - Q1300 steel plate for high-strength structure and preparation method and application thereof - Google Patents
Q1300 steel plate for high-strength structure and preparation method and application thereof Download PDFInfo
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- CN116926427A CN116926427A CN202310941279.2A CN202310941279A CN116926427A CN 116926427 A CN116926427 A CN 116926427A CN 202310941279 A CN202310941279 A CN 202310941279A CN 116926427 A CN116926427 A CN 116926427A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 81
- 239000010959 steel Substances 0.000 title claims abstract description 81
- 238000002360 preparation method Methods 0.000 title abstract description 9
- 238000005496 tempering Methods 0.000 claims abstract description 18
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 7
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 6
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 6
- 229910052742 iron Inorganic materials 0.000 claims abstract description 5
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 3
- 238000005096 rolling process Methods 0.000 claims description 52
- 238000010438 heat treatment Methods 0.000 claims description 25
- 238000010791 quenching Methods 0.000 claims description 25
- 238000000034 method Methods 0.000 claims description 24
- 230000000171 quenching effect Effects 0.000 claims description 23
- 238000007670 refining Methods 0.000 claims description 18
- 238000009749 continuous casting Methods 0.000 claims description 17
- 230000008569 process Effects 0.000 claims description 16
- 238000009628 steelmaking Methods 0.000 claims description 11
- 238000010079 rubber tapping Methods 0.000 claims description 10
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 10
- 230000009467 reduction Effects 0.000 claims description 8
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 6
- 238000004519 manufacturing process Methods 0.000 claims description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims description 5
- 238000010276 construction Methods 0.000 claims 1
- 229910052799 carbon Inorganic materials 0.000 abstract description 8
- 229910001566 austenite Inorganic materials 0.000 abstract description 4
- 230000009286 beneficial effect Effects 0.000 abstract description 4
- 229910000734 martensite Inorganic materials 0.000 abstract description 2
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 16
- 238000005266 casting Methods 0.000 description 13
- 239000002893 slag Substances 0.000 description 11
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 8
- 229910052786 argon Inorganic materials 0.000 description 8
- 239000011575 calcium Substances 0.000 description 8
- 229910052791 calcium Inorganic materials 0.000 description 8
- 208000004434 Calcinosis Diseases 0.000 description 7
- 230000002308 calcification Effects 0.000 description 7
- 230000001276 controlling effect Effects 0.000 description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 6
- CYUOWZRAOZFACA-UHFFFAOYSA-N aluminum iron Chemical compound [Al].[Fe] CYUOWZRAOZFACA-UHFFFAOYSA-N 0.000 description 6
- 238000007664 blowing Methods 0.000 description 6
- 235000008733 Citrus aurantifolia Nutrition 0.000 description 5
- 235000011941 Tilia x europaea Nutrition 0.000 description 5
- 239000004571 lime Substances 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 229910000519 Ferrosilicon Inorganic materials 0.000 description 4
- 229910000628 Ferrovanadium Inorganic materials 0.000 description 4
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 4
- 241000209094 Oryza Species 0.000 description 4
- 235000007164 Oryza sativa Nutrition 0.000 description 4
- 238000005275 alloying Methods 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 4
- 239000003795 chemical substances by application Substances 0.000 description 4
- 230000003009 desulfurizing effect Effects 0.000 description 4
- 238000010586 diagram Methods 0.000 description 4
- 238000007599 discharging Methods 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
- 229910052739 hydrogen Inorganic materials 0.000 description 4
- PNXOJQQRXBVKEX-UHFFFAOYSA-N iron vanadium Chemical compound [V].[Fe] PNXOJQQRXBVKEX-UHFFFAOYSA-N 0.000 description 4
- 239000002245 particle Substances 0.000 description 4
- 235000009566 rice Nutrition 0.000 description 4
- 238000005452 bending Methods 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 229910000604 Ferrochrome Inorganic materials 0.000 description 2
- 229910001309 Ferromolybdenum Inorganic materials 0.000 description 2
- 229910000592 Ferroniobium Inorganic materials 0.000 description 2
- 229910001200 Ferrotitanium Inorganic materials 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- 238000003723 Smelting Methods 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 235000013339 cereals Nutrition 0.000 description 2
- 238000007872 degassing Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 238000007667 floating Methods 0.000 description 2
- 230000004907 flux Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- ZFGFKQDDQUAJQP-UHFFFAOYSA-N iron niobium Chemical compound [Fe].[Fe].[Nb] ZFGFKQDDQUAJQP-UHFFFAOYSA-N 0.000 description 2
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000011574 phosphorus Substances 0.000 description 2
- 238000004321 preservation Methods 0.000 description 2
- 230000001105 regulatory effect Effects 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000009489 vacuum treatment Methods 0.000 description 2
- 229910000766 Aermet 100 Inorganic materials 0.000 description 1
- 229910000954 Medium-carbon steel Inorganic materials 0.000 description 1
- 229910006639 Si—Mn Inorganic materials 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 239000003153 chemical reaction reagent Substances 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 239000004567 concrete Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000032798 delamination Effects 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 239000010903 husk Substances 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000011572 manganese Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000005070 sampling Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910052719 titanium Inorganic materials 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
Abstract
The invention discloses a Q1300 steel plate for a high-strength structure, a preparation method and application thereof, and relates to the technical field of steel, wherein the steel plate comprises the following elements in parts by mass: c:0.20 to 0.26 percent of Si:0.18 to 0.32 percent of Mn:0.80 to 0.9 percent, less than or equal to 0.006 percent of P, less than or equal to 0.002 percent of S, and Nb:0.02% -0.032%, V:0.042% -0.049%, ti:0.012% -0.02%, ni:1.14 to 1.26 percent of Cr:0.35 to 0.45 percent of Mo:0.55% -0.68%, B:0.0012% -0.0022%, al:0.038% -0.075%, ca:0.001 to 0.003 percent of Fe and the balance of uncontrollable impurity elements. The invention fully utilizes the strength provided by the low-carbon martensite and the beneficial effect of low-temperature tempering residual austenite on low-temperature toughness by controlling the components of the Q1300 steel plate for the high-strength structure so as to stably obtain the required performance.
Description
Technical Field
The invention belongs to the technical field of steel, and particularly relates to a Q1300 steel plate for a high-strength structure, and a preparation method and application thereof.
Background
At present, the engineering machinery industry is an important component part of the mechanical industry, and as the mechanical industry continuously progresses towards the large-scale and light-weight, the strength grade of steel used by the engineering machinery industry is higher and higher. Compared with the steel for high-strength structures with the yield strength of 500MPa, 550MPa, 690MPa, 890MPa, 960MPa, 1100MPa and the like, the steel for high-strength structures with the yield strength of 1300MPa is used as the steel with the highest strength grade in the field of domestic engineering machinery at present. The steel plate with the grade strength is mainly used for key structural members such as a concrete pump truck, a telescopic boom of an automobile crane, a crawler crane base, a pulling plate, a large-tonnage hydraulic support and the like.
The traditional ultra-high strength steel such as AerMet100, 300M,4340 and the like is unfavorable for popularization and use because of high energy consumption, long production period or higher cost caused by more carbon content.
Disclosure of Invention
The present invention is directed to a Q1300 steel sheet for high strength structure, which solves at least one of the problems and disadvantages set forth in the background art.
The invention also provides a preparation method of the Q1300 steel plate for the high-strength structure.
The invention also provides application of the Q1300 steel plate for the high-strength structure.
Specifically, the first aspect of the invention consists of the following elements in percentage by mass:
c:0.20 to 0.26 percent of Si:0.18 to 0.32 percent of Mn:0.80 to 0.9 percent, less than or equal to 0.006 percent of P, less than or equal to 0.002 percent of S, and Nb:0.02% -0.032%, V:0.042% -0.049%, ti:0.012% -0.02%, ni:1.14 to 1.26 percent of Cr:0.35 to 0.45 percent of Mo:0.55% -0.68%, B:0.0012% -0.0022%, al:0.038% -0.075%, ca:0.001 to 0.003 percent of Fe and the balance of uncontrollable impurity elements.
According to one of the technical schemes of the Q1300 steel plate for the high-strength structure, at least the following beneficial effects are achieved:
the invention fully utilizes the strength provided by the low-carbon martensite and the beneficial effect of low-temperature tempering residual austenite on low-temperature toughness by controlling the components of the Q1300 steel plate for the high-strength structure so as to stably obtain the required performance. The component design is based on C-Si-Mn alloying, and is aided with Nb, V and Ti composite alloying refined crystal grains, ni is added to improve the low-temperature toughness of the material, and Cr, mo and a small amount of B are added to improve the hardenability of the material. The strength and toughness of the material are improved by means of dislocation strengthening, solid solution strengthening, precipitation strengthening, grain refinement and the like.
According to some embodiments of the invention, the yield strength rp0.2 of the Q1300 steel plate for high-strength structure is 1300MPa or more.
According to some embodiments of the invention, the tensile strength Rm of the Q1300 steel sheet for high-strength structure is 1350MPa to 1700MPa.
According to some embodiments of the invention, the elongation a50 of the Q1300 steel sheet for high strength structure is 8% or more.
According to some embodiments of the invention, the high strength structure is tested with Q1300 steel plate 180 DEG bend d.gtoreq.6a.
d is the diameter of the bend center, and a is the nominal thickness of the steel plate.
According to some embodiments of the invention, the high strength structural Q1300 steel plate has an average impact energy of 27J or more (-20 ℃).
According to some embodiments of the invention, the high strength structural Q1300 steel plate has an average impact energy of 27J or more (-40 ℃).
The impact test uses a Charpy V-notch specimen, the sampling direction is parallel to the rolling direction (longitudinal specimen), and the impact value in the table is the whole specimen (10 mm. Times.10 mm. Times.55 mm).
The second aspect of the invention provides a method for preparing a Q1300 steel plate for an upper high-strength structure, comprising the following steps:
sequentially carrying out converter steelmaking, LF furnace refining, VD refining, continuous casting, heating, rolling, quenching and tempering;
nitrogen is blown in the whole process of steel making and tapping of the converter;
the heating temperature is 1200-1240 ℃;
the rolling consists of rough rolling and finish rolling;
the initial rolling temperature of the rough rolling is above 1050 ℃.
According to one of the technical schemes of the preparation method, the preparation method at least has the following beneficial effects:
according to the preparation method, argon is blown in the whole process of the converter. And the dephosphorization operation is enhanced in smelting, the tapping P is strictly controlled to be less than or equal to 0.006 percent, and secondary P removal is carried out by adopting slag skimming after a furnace, so that the P content is fully reduced.
And (3) argon blowing and white slag making treatment of the LF furnace, and properly controlling the argon blowing and white slag keeping time to be full.
VD refining deep deoxidizing and desulfurizing, degassing (N, H) to remove impurities, uniform temperature and composition and pure steel. And (5) feeding silk. Deep deoxidizing and desulfurizing to spheroidize and denature the inclusions, which is favorable for floating large-particle inclusions.
The continuous casting adopts low superheat degree and constant pull speed steel casting, and simultaneously cooperates with advanced technologies such as dynamic soft reduction and the like, and performs whole-course protection casting so as to ensure good internal quality of billets. And controlling the rolling technology. The heating temperature and heating time of the steel billet are strictly controlled to obtain good austenite structure, and the uniformity of the temperature and the components of the steel billet is ensured.
Rough rolling adopts large pressure and low deformation rate to make deformation go deep into the core of the plate blank, so as to improve the internal quality of the steel plate; the finish rolling adopts the control of the accumulated rolling reduction, so that the rolling state structure is fully refined.
And (3) heat treatment: and a proper quenching and tempering process is adopted to obtain ideal tissue performance so as to obtain stable mechanical performance. Thereby producing a Q1300 steel sheet for high-strength structure having excellent properties.
According to some embodiments of the invention, the endpoint P mass percent of the converter steelmaking is below 0.006%.
According to some embodiments of the invention, the tapping temperature of the converter steelmaking is above 1550 ℃.
According to some embodiments of the invention, deoxidizing agents and alloys are added during tapping of the converter steelmaking.
According to some embodiments of the invention, the deoxidizer consists of an aluminum iron block and an aluminum iron wire.
According to some embodiments of the invention, top slag lime is added to the converter steelmaking.
According to some embodiments of the invention, the nitrogen is kept largely blown for 3min or more after steelmaking in the converter.
According to some embodiments of the invention, the heating temperature of the LF refining is above 1520 ℃.
According to some embodiments of the invention, the mass content of sulfur in the LF refining outbound molten steel is below 0.002%.
According to some embodiments of the invention, the LF furnace is refined and then added with calcium wire for a single calcification treatment.
According to some embodiments of the invention, the ferroboron is added after the primary calcification treatment.
According to some embodiments of the invention, the exit temperature of the LF refining is above 1630 ℃.
According to some embodiments of the invention, the VD refining is at an inbound temperature above 1620 ℃.
According to some embodiments of the invention, the vacuum hold time during VD refining is not less than 18 minutes.
According to some embodiments of the invention, the VD after refining ensures [ H ]. Ltoreq.1.3 ppm.
According to some embodiments of the invention, the VD is refined and then added to a calcium line for secondary calcification.
According to some embodiments of the invention, the break-open temperature during the VD refining process is 1580 ℃ to 1590 ℃.
According to some embodiments of the invention, the superheat degree of the continuous casting is controlled between 15 ℃ and 25 ℃.
According to some embodiments of the invention, the casting is protected throughout the casting process.
According to some embodiments of the invention, the casting furnace is topped up with a covering agent during the continuous casting process.
According to some embodiments of the invention, the continuous casting process uses carbonised rice husk for insulation.
According to some embodiments of the invention, the carbonized rice hulls are pushed into the tundish after being baked on the tundish cover for more than or equal to 10 minutes.
According to some embodiments of the invention, the ladle shroud is used for protecting argon gas from 20L/min to 60L/min in the continuous casting process.
According to some embodiments of the invention, the invasive nozzle seals argon gas 2L/min-10L/min during the continuous casting process.
According to some embodiments of the invention, the pull rate during continuous casting is 0.85m/min to 0.9m/min.
According to some embodiments of the invention, the continuous casting process uses low carbon mold flux or medium carbon steel mold flux.
According to some embodiments of the invention, the fluctuation of the liquid level during the continuous casting is within + -3 mm.
According to some embodiments of the invention, the initial rolling temperature of the rough rolling is equal to or higher than 1050 ℃.
According to some embodiments of the invention, the roughing has a triple reduction of greater than 18%.
According to some embodiments of the invention, the rough rolled intermediate stock has a thickness of three times or more the thickness of the stock.
According to some embodiments of the invention, the finish rolling is hot rolled, no water is required after finish rolling, and the finish rolling is air cooled to room temperature.
According to some embodiments of the invention, the heating temperature of the quenching is 820 ℃ to 840 ℃.
According to some embodiments of the invention, the quenching is performed for a time ranging from +20min to +30min.
According to some embodiments of the invention, the quench water pressure is above 0.8 bar.
According to some embodiments of the invention, after the quenching is discharged from the furnace, the quenching is quickly quenched to room temperature by adopting a compression roller type up-down symmetrical high-pressure water cooling, and the roller gap deviation is +/-1 mm.
According to some embodiments of the invention, the flow accuracy of the quenching nozzle is controlled to be +/-10 m 3 Within/h.
According to some embodiments of the invention, the tempering temperature is 190-210 ℃.
According to some embodiments of the invention, the tempering time is from 3.5+30min to 3.5+40min.
The invention in a third aspect provides an application of the Q1300 steel plate for the high-strength structure in preparing engineering machinery equipment.
Drawings
The present invention is further described below with reference to the accompanying drawings for the convenience of understanding by those skilled in the art.
FIG. 1 is a diagram showing a quenched microstructure of a steel sheet produced in example 1 of the present invention.
FIG. 2 is a metallographic structure diagram of a quenched and tempered state of a steel plate produced in example 1 of the present invention.
FIG. 3 is a graph showing fracture morphology of a tensile test piece of a steel plate according to example 1 of the present invention.
FIG. 4 is a graph showing the appearance of a cold-formed sample of a steel sheet according to example 1 of the present invention.
Detailed Description
The conception and the technical effects produced by the present invention will be clearly and completely described in conjunction with the embodiments below to fully understand the objects, features and effects of the present invention. It is apparent that the described embodiments are only some embodiments of the present invention, but not all embodiments, and that other embodiments obtained by those skilled in the art without inventive effort are within the scope of the present invention based on the embodiments of the present invention.
In the description of the present invention, the descriptions of the terms "one embodiment," "some embodiments," "illustrative embodiments," "examples," "specific examples," or "some examples," etc., mean that a particular feature, structure, material, or characteristic described in connection with the embodiment or example is included in at least one embodiment or example of the present invention. In this specification, schematic representations of the above terms do not necessarily refer to the same embodiments or examples. Furthermore, the particular features, structures, materials, or characteristics described may be combined in any suitable manner in any one or more embodiments or examples.
The specific conditions are not noted in the examples and are carried out according to conventional conditions or conditions recommended by the manufacturer. The reagents or apparatus used were conventional products commercially available without the manufacturer's attention.
Example 1
This example is a high-strength structural Q1300 steel sheet (12 mm Q1300D temper steel sheet) composed of the following elements in parts by weight:
c:0.21%, si:0.25%, mn:0.9%, P:0.004%, S:0.0008%, nb:0.023%, V:0.045%, ti:0.013%, ni:1.2%, cr:0.36%, mo:0.58%, B:0.0015%, alT:0.041%, ca:0.012% and the balance Fe and unavoidable impurities.
The production method of the Q1300 steel plate for the high-strength structure in the embodiment comprises the following steps:
s1, converter steelmaking:
the converter was charged with 119 tons of molten iron, 29.5 tons of scrap steel, 0.07% of terminal carbon (mass fraction), 0.004% of phosphorus (mass fraction), 320ppm of oxygen, and a tapping temperature of 1594 ℃.
In the tapping process, a sliding plate is used for double-gear, 305kg of ferrosilicon, 1215kg of manganese metal and 368kg of low-carbon ferrochrome are added in alloying, 312kg of aluminum iron is added in deoxidizer, 200 m of aluminum iron is added, and 350kg of lime is added in top slag.
S2, refining in an LF furnace:
the molten steel produced by the converter is refined by an LF furnace, a 3#B molten steel tank is used in the furnace, lime 1195kg and 60kg aluminum particles are added in the LF furnace at the station time of 85min, 600 m aluminum wires are fed in, 1396kg ferrotitanium, 1394kg ferromolybdenum, 276 metal manganese, 100kg ferrosilicon, 40kg ferrovanadium, 40kg ferroniobium, 150kg ferrovanadium, 440kg nickel plates and 20kg carbon powder are additionally added in the adjustment components, the calcium wire is fed in for calcification treatment, 12kg ferroboron is added after the calcium treatment, the outlet temperature is 1640 ℃, and the chemical components of the molten steel all hit the control range.
S3, VD refining:
carrying out VD refining on the outbound molten steel of the LF furnace; the inlet temperature of the VD furnace is 1626 ℃, the vacuum is pumped for 7 minutes and kept for 15 minutes, the total vacuum treatment is carried out for 22 minutes, and the vacuum breaking temperature is 1584 ℃. And (3) carrying out secondary calcification treatment by feeding the broken air with hydrogen of 1.3ppm and the broken air into a 250-meter calcium wire for 2 times, and discharging after soft blowing for 20min at a discharge temperature of 1548 ℃.
S4, continuous casting:
continuously casting the VD refined outbound molten steel; preparing a plate blank;
in the continuous casting process, a pouring furnace is filled with a covering agent, carbonized rice hulls are used for heat preservation, sibao peritectic steel covering slag is adopted, the whole casting process is protected, and the pulling speed is 0.85M/Min. The liquidus temperature is 1512 ℃, the minimum value of the temperature of the ladle molten steel is 1525 ℃, the maximum value is 1527 ℃, the minimum value of the superheat degree is 15 ℃, and the maximum value is 18 ℃. The level fluctuation of the crystallizer is +/-2 mm in the casting process.
S5, heating the plate blank:
heating the slab for 240 minutes, controlling the heating temperature at 1238 ℃ and then rolling;
s6, rolling:
rolling the heated plate blank;
the rolling adopts two-stage rolling, the initial rolling temperature of the rough rolling is 1082 ℃, and the rolling process adopts high-temperature and high-pressure rolling; the rough rolling is continuous with three-pass reduction rates of 19.6%, 20.5% and 18.5%, and the thickness of the intermediate billet is 60mm; the finish rolling is carried out by hot rolling, the finish rolling is carried out to obtain a steel plate with the thickness of 12mm, water is not required, and the steel plate is air-cooled to room temperature (25 ℃).
S7, quenching:
and carrying out off-line heat treatment quenching austenitizing on the rolled steel plate, wherein the quenching heating temperature is 900+/-10 ℃, the heating time is 27min, and after discharging, rapidly quenching to room temperature by adopting high-pressure water cooling, wherein the roll gap is regulated to 0.8mm, and the quenching water pressure is 0.85bar.
Nozzle flow accuracy + -6 m 3 /h。
S7, tempering:
and after quenching, directly tempering, wherein the tempering temperature is 250+/-10 ℃ and the tempering time is 55min.
The 12mm steel plate produced in this example was tested for performance: the yield strength is 1321MPa, the tensile strength is 1365MPa, the elongation is 10.2%, the cold bending is qualified (180 degrees, d=6a), the impact temperature is minus 40 ℃, the impact power is 55J,62J and 68J respectively, and the average impact power is 61.6J.
FIG. 1 is a diagram showing a metallographic structure of a quenched state of a steel sheet produced in this example; FIG. 2 is a metallographic structure diagram of quenched and tempered steel plate produced in this example; FIG. 3 is a graph showing fracture morphology of a tensile sample of a steel plate according to the present embodiment, from which no delamination or other anomalies in the core are known; fig. 4 is a graph of the appearance of a cold-formed sample of the steel plate of this example, and no cracking occurs in the bending radius.
Embodiment two:
this example is a high-strength structural Q1300 steel sheet (12 mm Q1300E temper steel sheet) composed of the following elements in parts by weight:
c:0.2%, si:0.24%, mn:0.92%, P:0.004%, S:0.0007%, nb:0.024%, V:0.046%, ti:0.013%, ni:1.2%, cr:0.37%, mo:0.58%, B:0.0016%, alT:0.042%, ca:0.012%, the balance being Fe and unavoidable impurities.
The production method of the Q1300 steel plate for the high-strength structure in the embodiment comprises the following steps:
s1, converter steelmaking:
the converter was charged with 120 tons of molten iron, 28 tons of scrap steel, 0.07% of terminal carbon (mass fraction), 0.004% of phosphorus (mass fraction), 319ppm of oxygen, and a tapping temperature of 1595 ℃.
In the tapping process, a sliding plate is used for double-gear, 306kg of ferrosilicon, 1215kg of manganese metal and 368kg of low-carbon ferrochrome are added in alloying, 312kg of aluminum iron is added in deoxidizer, 200 m of aluminum iron is added, and 350kg of lime is added in top slag.
S2, refining in an LF furnace:
the molten steel produced by the converter is refined by an LF furnace, a 3#B molten steel tank is used in the furnace, lime 1195kg and 60kg aluminum particles are added in the LF furnace at the station time of 85min, 600 m aluminum wires are fed in, 1396kg ferrotitanium, 1394kg ferromolybdenum, 276 metal manganese, 100kg ferrosilicon, 40kg ferrovanadium, 40kg ferroniobium, 150kg ferrovanadium, 440kg nickel plates and 20kg carbon powder are additionally added in the adjustment components, the calcium wire is fed in for calcification treatment, 12kg ferroboron is added after the calcium treatment, the outlet temperature is 1640 ℃, and the chemical components of the molten steel all hit the control range.
S3, VD refining:
carrying out VD refining on the outbound molten steel of the LF furnace; vacuum is pumped for 7min at the start-up temperature of 1628 ℃ for 16min, the total vacuum treatment is carried out for 23min, and the vacuum breaking temperature is 1584 ℃.
And (3) carrying out secondary calcification treatment by feeding the broken air with hydrogen of 1.3ppm and the broken air into a 250-meter calcium wire for 2 times, and discharging after soft blowing for 20min at 1550 ℃.
S4, continuous casting:
continuously casting the VD refined outbound molten steel; preparing a plate blank;
in the continuous casting process, a pouring furnace is filled with a covering agent, carbonized rice hulls are used for heat preservation, sibao peritectic steel covering slag is adopted, the whole casting process is protected, and the pulling speed is 0.85M/Min. The liquidus temperature is 1510 ℃, the temperature of the ladle molten steel is 1523 ℃ at the lowest value, 1525 ℃ at the highest value, 16 ℃ at the lowest value and 20 ℃ at the highest value. The level fluctuation of the crystallizer is +/-2 mm in the casting process.
S5, heating the plate blank:
heating the slab for 250 minutes, controlling the heating temperature at 1240 ℃ and then rolling;
s6, rolling:
rolling the heated plate blank;
the rolling adopts two-stage rolling, the initial rolling temperature of rough rolling is 1080 ℃, and the rolling process adopts high-temperature high-pressure rolling; the rough rolling is continuous with three-pass reduction rates of 19.8%, 20.4% and 19.5%, and the thickness of the intermediate billet is 60mm; the finish rolling is carried out by hot rolling, the finish rolling is carried out to obtain a steel plate with the thickness of 12mm, water is not required, and the steel plate is air-cooled to room temperature (25 ℃).
S7, quenching:
and carrying out off-line heat treatment quenching austenitizing on the rolled steel plate, wherein the quenching heating temperature is 900+/-10 ℃, the heating time is 28min, and after discharging, rapidly quenching to room temperature by adopting high-pressure water cooling, wherein the roll gap is regulated to 0.8mm, and the quenching water pressure is 0.86bar.
Nozzle flow accuracy + -5 m 3 /h。
S7, tempering:
and after quenching, directly tempering, wherein the tempering temperature is 250+/-10 ℃ and the tempering time is 56min.
The 12mm steel plate produced in this example was tested for performance: the yield strength is 1325MPa, the tensile strength is 1366MPa, the elongation is 11.2%, the cold bending is qualified (180 degrees, d=6a), the impact temperature is minus 40 ℃, the impact energy is 58J,64J,70J respectively, and the average impact energy is 64J.
In summary, according to the preparation method of the invention, argon is blown in the whole process of the converter. And the dephosphorization operation is enhanced in smelting, the tapping P is strictly controlled to be less than or equal to 0.006 percent, and secondary P removal is carried out by adopting slag skimming after a furnace, so that the P content is fully reduced. And (3) argon blowing and white slag making treatment of the LF furnace, and properly controlling the argon blowing and white slag keeping time to be full. Vacuum VD, deep deoxidizing and desulfurizing, degassing (N, H) to remove impurities, uniform temperature and composition and pure steel. And (5) feeding silk. Deep deoxidizing and desulfurizing to spheroidize and denature the inclusions, which is favorable for floating large-particle inclusions. The continuous casting adopts low superheat degree and constant pull speed steel casting, and simultaneously cooperates with advanced technologies such as dynamic soft reduction and the like, and performs whole-course protection casting so as to ensure good internal quality of billets. And controlling the rolling technology. The heating temperature and heating time of the steel billet are strictly controlled to obtain good austenite structure, and the uniformity of the temperature and the components of the steel billet is ensured. Rough rolling adopts large pressure and low deformation rate to make deformation go deep into the core of the plate blank, so as to improve the internal quality of the steel plate; the finish rolling adopts the control of the accumulated rolling reduction, so that the rolling state structure is fully refined. And (3) heat treatment: and a proper quenching and tempering process is adopted to obtain ideal tissue performance so as to obtain stable mechanical performance. Thereby producing a Q1300 steel sheet for high-strength structure having excellent properties.
While the foregoing is directed to embodiments of the present invention, other and further details of the invention may be had by the present invention, it should be understood that the foregoing description is merely illustrative of the present invention and that no limitations are intended to the scope of the invention, except insofar as modifications, equivalents, improvements or modifications are within the spirit and principles of the invention.
Claims (10)
1. The Q1300 steel plate for the high-strength structure is characterized by comprising the following elements in percentage by mass:
c:0.20 to 0.26 percent of Si:0.18 to 0.32 percent of Mn:0.80 to 0.9 percent, less than or equal to 0.006 percent of P, less than or equal to 0.002 percent of S, and Nb:0.02% -0.032%, V:0.042% -0.049%, ti:0.012% -0.02%, ni:1.14 to 1.26 percent of Cr:0.35 to 0.45 percent of Mo:0.55% -0.68%, B:0.0012% -0.0022%, al:0.038% -0.075%, ca:0.001 to 0.003 percent of Fe and the balance of uncontrollable impurity elements.
2. A method for producing the Q1300 steel sheet for high strength structure according to claim 1, comprising the steps of:
sequentially carrying out converter steelmaking, LF furnace refining, VD refining, continuous casting, heating, rolling, quenching and tempering;
nitrogen is blown in the whole process of steel making and tapping of the converter;
the rolling consists of rough rolling and finish rolling;
the heating temperature is 1200-1240 ℃;
the initial rolling temperature of the rough rolling is above 1050 ℃.
3. The method according to claim 2, wherein the superheat of the continuous casting is controlled between 15 ℃ and 25 ℃.
4. The method of claim 2, wherein the roughing has a triple reduction of greater than 18%.
5. The method according to claim 2, wherein the quenching is performed at a heating temperature of 820 ℃ to 840 ℃.
6. The method according to claim 2, wherein the quenching is performed for a period of time ranging from +20min to +30min.
7. The method according to claim 2, wherein the quench water pressure is above 0.8 bar.
8. The method of claim 2, wherein the tempering is at a temperature of 190 ℃ to 210 ℃.
9. The method of claim 2, wherein the tempering time is from 3.5+30min to 3.5+40min.
10. Use of the Q1300 steel sheet for high strength construction according to claim 1 for manufacturing engineering machinery.
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