CN114622137A - Advanced high-strength steel with better fatigue performance and preparation method thereof - Google Patents
Advanced high-strength steel with better fatigue performance and preparation method thereof Download PDFInfo
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- 239000010959 steel Substances 0.000 title claims abstract description 86
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 85
- 238000002360 preparation method Methods 0.000 title abstract description 8
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 13
- 238000012360 testing method Methods 0.000 claims abstract description 13
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 11
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 11
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 9
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 57
- 229910052742 iron Inorganic materials 0.000 claims description 27
- 238000000034 method Methods 0.000 claims description 21
- 238000005096 rolling process Methods 0.000 claims description 21
- 238000000137 annealing Methods 0.000 claims description 18
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 17
- 239000002893 slag Substances 0.000 claims description 15
- 238000010438 heat treatment Methods 0.000 claims description 13
- 238000007670 refining Methods 0.000 claims description 13
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 12
- 238000005266 casting Methods 0.000 claims description 12
- 238000001816 cooling Methods 0.000 claims description 12
- 238000009749 continuous casting Methods 0.000 claims description 11
- 239000010936 titanium Substances 0.000 claims description 11
- 238000007664 blowing Methods 0.000 claims description 10
- 238000003723 Smelting Methods 0.000 claims description 9
- 239000011572 manganese Substances 0.000 claims description 8
- 229910001257 Nb alloy Inorganic materials 0.000 claims description 7
- 229910001069 Ti alloy Inorganic materials 0.000 claims description 7
- 229910045601 alloy Inorganic materials 0.000 claims description 7
- 239000000956 alloy Substances 0.000 claims description 7
- 238000011068 loading method Methods 0.000 claims description 7
- 239000000463 material Substances 0.000 claims description 7
- 229910052717 sulfur Inorganic materials 0.000 claims description 7
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 6
- 229910000592 Ferroniobium Inorganic materials 0.000 claims description 6
- -1 aluminum manganese titanium Chemical compound 0.000 claims description 6
- 229910052786 argon Inorganic materials 0.000 claims description 6
- 238000010079 rubber tapping Methods 0.000 claims description 6
- 238000004519 manufacturing process Methods 0.000 claims description 5
- 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 claims description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 4
- 208000004434 Calcinosis Diseases 0.000 claims description 3
- 229910000616 Ferromanganese Inorganic materials 0.000 claims description 3
- 229910000519 Ferrosilicon Inorganic materials 0.000 claims description 3
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 3
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 3
- 239000002253 acid Substances 0.000 claims description 3
- 229910052782 aluminium Inorganic materials 0.000 claims description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 3
- 230000002308 calcification Effects 0.000 claims description 3
- 239000003795 chemical substances by application Substances 0.000 claims description 3
- 230000003749 cleanliness Effects 0.000 claims description 3
- 238000005097 cold rolling Methods 0.000 claims description 3
- 238000002425 crystallisation Methods 0.000 claims description 3
- 230000008025 crystallization Effects 0.000 claims description 3
- 229910002804 graphite Inorganic materials 0.000 claims description 3
- 239000010439 graphite Substances 0.000 claims description 3
- DALUDRGQOYMVLD-UHFFFAOYSA-N iron manganese Chemical compound [Mn].[Fe] DALUDRGQOYMVLD-UHFFFAOYSA-N 0.000 claims description 3
- 229910052749 magnesium Inorganic materials 0.000 claims description 3
- 239000011777 magnesium Substances 0.000 claims description 3
- 230000014759 maintenance of location Effects 0.000 claims description 3
- PYLLWONICXJARP-UHFFFAOYSA-N manganese silicon Chemical compound [Si].[Mn] PYLLWONICXJARP-UHFFFAOYSA-N 0.000 claims description 3
- 238000012544 monitoring process Methods 0.000 claims description 3
- 229910052760 oxygen Inorganic materials 0.000 claims description 3
- 239000001301 oxygen Substances 0.000 claims description 3
- 239000002245 particle Substances 0.000 claims description 3
- 238000005554 pickling Methods 0.000 claims description 3
- 230000001681 protective effect Effects 0.000 claims description 3
- 238000005070 sampling Methods 0.000 claims description 3
- 238000003756 stirring Methods 0.000 claims description 3
- 239000011593 sulfur Substances 0.000 claims description 3
- 238000012546 transfer Methods 0.000 claims description 3
- 238000005406 washing Methods 0.000 claims description 3
- 230000001276 controlling effect Effects 0.000 description 14
- 239000011651 chromium Substances 0.000 description 9
- 239000000126 substance Substances 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 4
- 238000009661 fatigue test Methods 0.000 description 4
- 239000010703 silicon Substances 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- 230000002159 abnormal effect Effects 0.000 description 2
- 238000009529 body temperature measurement Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000001514 detection method Methods 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910001562 pearlite Inorganic materials 0.000 description 2
- 238000004088 simulation Methods 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229910001021 Ferroalloy Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 125000004432 carbon atom Chemical group C* 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- ZFGFKQDDQUAJQP-UHFFFAOYSA-N iron niobium Chemical compound [Fe].[Fe].[Nb] ZFGFKQDDQUAJQP-UHFFFAOYSA-N 0.000 description 1
- 238000010907 mechanical stirring Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000006467 substitution reaction Methods 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
- C21D1/26—Methods of annealing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- 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
- C21D8/0273—Final recrystallisation annealing
-
- 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
- C22C33/06—Making ferrous alloys by melting using master alloys
-
- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Treatment Of Steel In Its Molten State (AREA)
Abstract
The invention discloses an advanced high-strength steel with better fatigue performance and a preparation method thereof, relating to the field of advanced high-strength steel with better fatigue performance and preparation methods thereof, and comprising the following components in percentage by mass: c: 0.10 to 0.12%, Si: 0.45-0.55%, Mn: 1.20-1.50%, P: less than or equal to 0.025 percent, S: less than or equal to 0.015 percent, Al: 0.015% -0.050%, V: 0.09-0.12%, Cr: 0.70-1.10%, Ni: 1.75 to 2.25%, and the balance being Fe and unavoidable impurities. The invention obviously improves the strength and fatigue limit of steel and improves the fatigue performance; meanwhile, the plasticity and the impact toughness are not changed, the working condition of the upper sheet body of the auxiliary frame can be met, and the fatigue endurance test is passed.
Description
Technical Field
The invention relates to the field of steel manufacturing, in particular to advanced high-strength steel with better fatigue performance and a preparation method thereof.
Background
When the auxiliary frame of a certain vehicle type is used for a bench braking endurance test, the auxiliary frame cracks after 9 ten thousand times of test and 9 ten thousand times of test, and the test requirement is 30 ten thousand times. The main position of fracture is at sub vehicle frame upper segment body, and the fracture position corresponds about. Wherein, the crack length is about 8mm deep, the surface quality of the plate is good, and the plate has no appearance defect.
After failure analysis, the results are: the metallographic structure at the crack source and the base material was ferrite pearlite and was not abnormal. The average value of microhardness of the crack source and the parent metal is 218HV, and the hardness is not abnormal.
And detecting chemical components of the product to find that the chemical components meet the standard requirements. See in particular the table below.
TABLE 1 chemical composition and Standard Specification/% of the upper piece bulk
The microscopic morphology of the fracture is observed by using a scanning electron microscope, and the fracture is found to have fatigue characteristics such as a shell line and the like, and belongs to fatigue cracking. The mean value of the microhardness of the crack source is 218HV, and the corresponding tensile strength is 700 MPa. The fatigue limit at the crack origin, which is 0.38MPa +0.43 strength limit, is calculated, here 301MPa, and according to the simulation analysis results, the stress at the crack origin should be around 350MPa, so that under loading, the stress at the crack origin is greater than its fatigue limit, causing cracking.
As the material used by the upper sheet body of the auxiliary frame is QStE420TM, the tensile strength range is more than 380MPa, the corresponding fatigue limit range is more than 163MPa, and the stress requirement of the crack source under the working condition of the brake endurance test is far lower, a steel material with higher strength and better fatigue performance is needed.
In the chemical composition of the cracking part of the upper sheet body, the sum of the three elements of V + Ti + Nb is about 0.056%, the content of alloy elements is low, and the yield and the tensile strength of the steel are poor, so that the content of corresponding elements needs to be changed, and the tensile strength is mainly improved.
Disclosure of Invention
The invention aims to overcome the defects in the prior art and provide the advanced high-strength steel with better fatigue performance and the preparation method thereof, which are used for replacing QStE420TM as the upper sheet body material. The steel meets the molding requirement of the upper sheet of the auxiliary frame, the elongation of the steel meets the requirement that QStE420TM stipulate that the elongation is more than or equal to 16 percent, and the fatigue limit of the steel also meets 350MPa of simulation analysis. In a brake endurance fatigue test, the brake endurance fatigue test can reach 30 ten thousand times specified by a standard, and the upper sheet body is ensured not to crack.
The purpose of the invention is achieved by the following technical scheme: the advanced high-strength steel with better fatigue performance comprises the following components in percentage by mass:
c: 0.10 to 0.12%, Si: 0.45-0.55%, Mn: 1.20-1.50%, P: less than or equal to 0.025 percent, S: less than or equal to 0.015 percent, Al: 0.015% -0.050%, V: 0.09-0.12%, Cr: 0.70-1.10%, Ni: 1.75 to 2.25%, and the balance being Fe and unavoidable impurities.
The preparation method of the advanced high-strength steel with better fatigue performance comprises the following steps:
1) pretreating molten iron: adopting magnesium particles for molten iron blowing in a molten iron tank to carry out molten iron desulphurization, controlling the mass percent of sulfur in the molten iron to be below 0.015 percent and controlling the temperature to be not lower than 1250 ℃, and completely skimming slag on the surface of the molten iron after the desulphurization is finished;
2) smelting in a converter: smelting the molten iron obtained after pretreatment in the step 1) in a converter, adding slag-forming materials 3 minutes before the end point, monitoring and controlling in real time in the whole process without adding Ti and Nb alloy elements, and adopting bottom-blown oxygen to ensure that the mass percentages of all the elements meet that C is less than or equal to 0.12%, Si is less than or equal to 0.60%, Mn is less than or equal to 1.60%, P is less than or equal to 0.060%, and S is less than or equal to 0.060%;
3) refining: step 2), the molten steel smelted by the transfer furnace enters a refining furnace, refining is carried out by adopting a white slag method, and the white slag retention time is more than 12 minutes; feeding a 500-700 m SiCa wire into the refined molten steel for calcification treatment, and soft-blowing argon for 10-20 minutes to remove impurities in the steel and improve the cleanliness of the molten steel; finely adjusting components by adopting ferromanganese, ferrosilicon, ferroniobium and nickel plate alloy, and adjusting Ti components by using a titanium wire; adjusting Al component by using an aluminum wire;
4) continuous casting: continuously casting the molten steel refined in the step 3), wherein the molten steel is subjected to protective pouring in the whole process in the continuous casting process, the superheat degree of the molten steel is controlled to be between 15 and 30 ℃, tundish covering agent and crystallizer protecting slag are used, and both the crystallizer and secondary cooling adopt weak cooling;
5) hot continuous rolling: carrying out hot continuous rolling on the steel plate continuously cast in the step 4), adopting a direct loading or hot loading system, adopting micro-positive pressure control for a heating furnace to ensure a reducing atmosphere, controlling the tapping temperature to be above 1190 ℃, controlling the rough rolling temperature to be above 1040 ℃, controlling the final rolling temperature to be above 890 ℃, and controlling the coiling temperature to be above 600 ℃;
6) acid washing and cold continuous rolling: pickling and cold continuous rolling the steel plate subjected to hot continuous rolling in the step 5), wherein the cold rolling reduction rate is controlled to be 55-75%;
7) and (3) continuous annealing: continuously annealing the steel plate obtained in the step 6), wherein the annealing temperature is controlled to be (820 +/-10) ° C;
8) leveling: and cooling and carrying out flattening treatment after the annealing in the step 7).
As a further technical scheme, in the step 2), 800kg of synthetic slag is firstly added at the bottom of a ladle before tapping of a converter; the aluminum manganese titanium is adopted for deoxidation, the dosage is 2kg/t molten steel, when one quarter of the molten steel is placed, silicon manganese, medium manganese, aluminum manganese titanium and ferrocolumbium are added, and the addition is finished when the molten steel is discharged to three quarters.
As a further technical scheme, in the step 3), a graphite electrode is inserted from the top of the refining furnace for heating, so that the temperature loss caused by argon blowing and feeding is compensated; and after heating is finished, measuring temperature and testing components, and circulating for multiple times of heating, measuring temperature, sampling, testing and feeding until the components of the molten steel meet the standard requirements.
As a further technical scheme, in the step 4), during continuous casting, the ladle containing the molten steel refined in the step 3) is transported to a rotary table, the rotary table rotates to a casting position and then injects the molten steel into a tundish, and the tundish distributes the molten steel into each crystallizer through a water gap; the crystallizer is one of the core equipments of the continuous casting machine, which shapes the casting and rapidly solidifies the crystals. The casting in the crystallizer is pulled out under the combined action of a withdrawal and straightening machine and a crystallization vibration device, and is cut into slabs with certain length after cooling and electromagnetic stirring.
The invention has the beneficial effects that:
1. the invention cancels Ti and Nb alloy elements, thus improving the smelting efficiency;
2. the tensile strength is obviously improved by increasing the content of the V element; meanwhile, the plasticity and the impact toughness are not changed;
3. the invention improves the tensile strength and the fatigue property and properly improves the toughness by newly increasing the contents of Cr and Ni elements; the working condition of the upper piece body of the auxiliary frame can be met, and the fatigue endurance test can be passed theoretically.
Detailed Description
Example (b): the advanced high-strength steel with better fatigue performance comprises the following components in percentage by mass:
c: 0.10 to 0.12%, Si: 0.45-0.55%, Mn: 1.20-1.50%, P: less than or equal to 0.025 percent, S: less than or equal to 0.015 percent, Al: 0.015% -0.050%, V: 0.09-0.12%, Cr: 0.70-1.10%, Ni: 1.75 to 2.25%, and the balance being Fe and unavoidable impurities.
In order to obtain better tensile strength and toughness, the invention mainly improves the content of C, V, cancels Ti and Nb alloy elements and newly adds two alloy elements of Cr and Ni on the basis of QStE420TM detection results and standard provisions. The following are the main elements and effects of the invention
Carbon: the carbon atoms play a role in interstitial solid solution strengthening and are the most economical and effective strengthening mode in steel. The carbon content in the steel increases, the yield and tensile strength increase, but the plasticity decreases, and in order to prevent the plasticity from decreasing too much, the carbon content slightly increases but does not change much.
Silicon: silicon is a common element in steel, is dissolved in ferrite in the steel in a solid solution manner, has a remarkable solid solution strengthening effect, but the silicon reduces the uniform plasticity of the steel, so the content of the silicon is controlled to be constant.
Manganese: manganese exists in the steel mainly in a solid solution state, and the strength increment of 40-60MPa can be generated approximately every 1% of solid solution manganese, and meanwhile, the toughness of the steel is favorably improved.
Vanadium: the vanadium has obvious effect of grain refinement and dispersion strengthening, and the tensile strength can be obviously increased by adding a small amount of vanadium.
Chromium: chromium significantly improves strength, hardness and wear resistance, and within a certain range, improves plasticity and elongation to a certain extent. Chromium is a medium-strength carbide-forming element and is the main component of stainless steel.
Nickel: the nickel strengthens ferrite, refines and increases pearlite, improves the strength of the steel and has small influence on the plasticity of the steel. Improve the fatigue properties of the steel and reduce the susceptibility of the steel to chipping.
The preparation method of the advanced high-strength steel with better fatigue performance comprises the following steps:
1) pretreating molten iron: and (3) carrying out molten iron desulphurization in the molten iron tank by adopting the injected magnesium particles, controlling the mass percent of sulfur in the molten iron to be below 0.015 percent and controlling the temperature to be not lower than 1250 ℃, and completely removing slag on the surface of the molten iron after the desulphurization is finished. The pretreatment of molten iron refers to a treatment process for removing impurity elements from molten iron before the molten iron is added into a steel-making furnace. The common process methods are as follows: bulk iron runner method, in-ladle blowing method, in-ladle mechanical stirring method, etc. In this embodiment, a hot metal ladle blowing method is adopted.
2) Smelting in a converter: smelting the molten iron obtained after pretreatment in the step 1) in a converter, adding slag-forming materials 3 minutes before the end point, monitoring and controlling in real time in the whole process without adding Ti and Nb alloy elements, and adopting bottom-blown oxygen to ensure that the mass percentages of the elements meet that C is less than or equal to 0.12%, Si is less than or equal to 0.60%, Mn is less than or equal to 1.60%, P is less than or equal to 0.060%, and S is less than or equal to 0.060%. The converter smelting is to take molten iron, scrap steel and ferroalloy as main raw materials, and finish the steel-making process in a converter by means of the physical heat of the molten iron and the heat generated by the chemical reaction between the components of the molten iron without the help of external energy. Before tapping of a converter, firstly adding 800kg of synthetic slag at the bottom of a ladle; the aluminum manganese titanium is adopted for deoxidation, the dosage is 2kg/t molten steel, when one quarter of the molten steel is placed, silicon manganese, medium manganese, aluminum manganese titanium and ferrocolumbium are added, and the addition is finished when the molten steel is discharged to three quarters.
3) Refining: step 2), the molten steel smelted by the transfer furnace enters a refining furnace, refining is carried out by adopting a white slag method, and the white slag retention time is more than 12 minutes; feeding 500-700 m SiCa wire into the refined molten steel for calcification treatment, and soft-blowing argon for 10-20 minutes to remove impurities in the steel (also playing a role in accelerating alloy melting and realizing uniform components), so as to improve the cleanliness of the molten steel; carrying out component fine adjustment by adopting ferromanganese, ferrosilicon, ferrocolumbium and nickel plate alloy, and adjusting Ti component by using a titanium wire; the Al content was adjusted by using an aluminum wire. During the refining process, a graphite electrode is inserted from the top of the refining furnace for heating, so that the temperature loss caused by argon blowing and feeding is compensated; after heating is completed, temperature measurement and component testing are carried out, and multiple cycles of heating, temperature measurement, sampling, testing and feeding are carried out until the components of the molten steel meet the standard requirements (namely the mass percentage requirements in the embodiment).
4) Continuous casting: and (3) continuously casting the refined molten steel in the step 3), wherein the molten steel is subjected to protective pouring in the whole process in the continuous casting process, the superheat degree of the molten steel is controlled to be between 15 and 30 ℃, a special tundish covering agent and crystallizer protecting slag are used, and a liquid level automatic control system is adopted in the crystallizer to ensure the stability of the liquid level. Meanwhile, the casting is carried out at a constant pulling speed, the surface quality of a casting blank is guaranteed, the crystallizer and the secondary cooling both adopt weak cooling, and the specific water amount is 0.9-1.2L/Kg. During continuous casting, the ladle containing the molten steel refined in the step 3) is transported to a rotary table, the rotary table rotates to a casting position, the molten steel is poured into a tundish, and the tundish distributes the molten steel into each crystallizer through a water gap. The crystallizer is one of the core equipments of the continuous casting machine, which shapes the casting and rapidly solidifies the crystals. The casting in the crystallizer is pulled out under the combined action of a withdrawal and straightening machine and a crystallization vibration device, and is cut into slabs with certain length after cooling and electromagnetic stirring.
5) Hot continuous rolling: carrying out hot continuous rolling on the steel plate continuously cast in the step 4), adopting a direct loading or hot loading system on the basis of reasonable control of chemical components of the steel base, adopting micro-positive pressure control for a heating furnace to ensure a reducing atmosphere, controlling the tapping temperature to be above 1190 ℃, controlling the rough rolling temperature to be above 1040 ℃, controlling the final rolling temperature to be above 890 ℃, and controlling the coiling temperature to be above 600 ℃;
6) acid washing and cold continuous rolling: pickling and cold continuous rolling are carried out on the steel plate subjected to hot continuous rolling in the step 5), and the cold rolling reduction is controlled to be 55-75% according to the actual condition and characteristics of the steel grade;
7) and (3) continuous annealing: continuously annealing the steel plate obtained in the step 6), wherein the annealing temperature is controlled to be (820 +/-10) DEG C. The purpose of cold strip annealing is to reduce the intensive cold work hardening and to improve the formability of the sheet. Generally, annealing is carried out above the recrystallization temperature, which results in a soft structure with good cold formability. During annealing, there is a possibility to link recrystallization to a change in the chemical composition of the steel, which involves reactive annealing. If high strength is desired for the processing and use of the sheet and no special requirements are made for cold formability, a state between the fully roll-hardened structure and the fully recrystallized structure can be obtained by annealing. At this time, the heat treatment serves as a recovery and partial recrystallization annealing.
8) Leveling: and cooling and carrying out flattening treatment after the annealing in the step 7). And after the leveling treatment, the finished product is inspected, and then the product can be packaged and delivered out of the factory.
In order to obtain better tensile strength and toughness, the advanced high-strength steel mainly improves the content of C, V, eliminates Ti and Nb alloy elements and newly adds two alloy elements of Cr and Ni on the basis of QStE420TM detection results and standard regulations. The cold stamping forming requirement of the upper sheet of the auxiliary frame can be met, the elongation rate meets the requirement that QStE420TM is regulated to be more than or equal to 16 percent, and the fatigue limit can reach more than 350 MPa. In a brake endurance fatigue test, the brake endurance fatigue test can reach 30 ten thousand times specified by a standard, and the upper piece body is ensured not to crack. In general, the invention cancels Ti and Nb alloy elements, thus improving the smelting efficiency; by increasing the content of the V element, the tensile strength and the fatigue limit are obviously improved, and the fatigue performance is improved; the content of Cr and Ni elements is increased, the tensile strength and the fatigue property are improved, the toughness is properly improved, and meanwhile, the plasticity and the impact toughness are not changed, so that the working condition of the upper sheet body of the auxiliary frame in use can be met.
It should be understood that equivalent substitutions and changes to the technical solution and the inventive concept of the present invention should be made by those skilled in the art to the protection scope of the appended claims.
Claims (5)
1. An advanced high-strength steel with better fatigue performance is characterized in that: comprises the following components in percentage by mass: c: 0.10 to 0.12%, Si: 0.45-0.55%, Mn: 1.20-1.50%, P: less than or equal to 0.025%, S: less than or equal to 0.015 percent, Al: 0.015% -0.050%, V: 0.09-0.12%, Cr: 0.70-1.10%, Ni: 1.75 to 2.25%, and the balance being Fe and unavoidable impurities.
2. A method of manufacturing an advanced high strength steel with better fatigue properties according to claim 1, characterized in that: the method comprises the following steps:
1) pretreatment of molten iron: adopting magnesium particles for molten iron blowing in a molten iron tank to carry out molten iron desulphurization, controlling the mass percent of sulfur in the molten iron to be below 0.015 percent and controlling the temperature to be not lower than 1250 ℃, and completely skimming slag on the surface of the molten iron after the desulphurization is finished;
2) smelting in a converter: smelting the molten iron obtained after pretreatment in the step 1) in a converter, adding slag-forming materials 3 minutes before the end point, monitoring and controlling in real time in the whole process without adding Ti and Nb alloy elements, and adopting bottom-blown oxygen to ensure that the mass percentages of all the elements meet that C is less than or equal to 0.12%, Si is less than or equal to 0.60%, Mn is less than or equal to 1.60%, P is less than or equal to 0.060%, and S is less than or equal to 0.060%;
3) refining: step 2), the molten steel smelted by the transfer furnace enters a refining furnace, refining is carried out by adopting a white slag method, and the white slag retention time is more than 12 minutes; feeding a 500-700 m SiCa wire into the refined molten steel for calcification treatment, and soft-blowing argon for 10-20 minutes to remove impurities in the steel and improve the cleanliness of the molten steel; carrying out component fine adjustment by adopting ferromanganese, ferrosilicon, ferrocolumbium and nickel plate alloy, and adjusting Ti component by using a titanium wire; adjusting Al component by using an aluminum wire;
4) continuous casting: continuously casting the molten steel refined in the step 3), wherein the molten steel is subjected to protective pouring in the whole process in the continuous casting process, the superheat degree of the molten steel is controlled to be between 15 and 30 ℃, tundish covering agent and crystallizer protecting slag are used, and both the crystallizer and secondary cooling adopt weak cooling;
5) hot continuous rolling: carrying out hot continuous rolling on the steel plate continuously cast in the step 4), adopting a direct loading or hot loading system, adopting micro-positive pressure control for a heating furnace to ensure a reducing atmosphere, controlling the tapping temperature to be above 1190 ℃, controlling the rough rolling temperature to be above 1040 ℃, controlling the final rolling temperature to be above 890 ℃, and controlling the coiling temperature to be above 600 ℃;
6) acid washing and cold continuous rolling: pickling and cold continuous rolling the steel plate subjected to hot continuous rolling in the step 5), wherein the cold rolling reduction rate is controlled to be 55-75%;
7) and (3) continuous annealing: continuously annealing the steel plate obtained in the step 6), wherein the annealing temperature is controlled to be 820 +/-10 ℃;
8) leveling: and cooling and carrying out flattening treatment after the annealing in the step 7).
3. The production method according to claim 2, characterized in that: in the step 2), 800kg of synthetic slag is firstly added into the bottom of a ladle before tapping of the converter; the aluminum manganese titanium is adopted for deoxidation, the dosage is 2kg/t molten steel, when one quarter of the molten steel is placed, silicon manganese, medium manganese, aluminum manganese titanium and ferrocolumbium are added, and the addition is finished when the molten steel is discharged to three quarters.
4. The production method according to claim 2, characterized in that: in the step 3), a graphite electrode is inserted from the top of the refining furnace for heating, so that the temperature loss caused by argon blowing and feeding is compensated; and after heating is finished, measuring temperature and testing components, and circulating for multiple times of heating, measuring temperature, sampling, testing and feeding until the components of the molten steel meet the standard requirements.
5. The production method according to claim 2, characterized in that: in the step 4), during continuous casting, the ladle containing the molten steel refined in the step 3) is transported to a rotary table, the rotary table rotates to a pouring position, the molten steel is poured into a tundish, and the tundish distributes the molten steel to each crystallizer through a water gap; the casting in the crystallizer is pulled out under the combined action of a withdrawal and straightening machine and a crystallization vibration device, and is cut into slabs with certain length after cooling and electromagnetic stirring.
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Citations (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07150291A (en) * | 1993-12-01 | 1995-06-13 | Kobe Steel Ltd | High strength hot rolled steel sheet for working excellent in fatigue property |
| CN1847412A (en) * | 2005-04-12 | 2006-10-18 | 万向钱潮股份有限公司 | Annealing process of 20CrMnTi steel for cold extrusion |
| JP2007321201A (en) * | 2006-06-01 | 2007-12-13 | Kobe Steel Ltd | High-strength hot-rolled steel plate superior in strength-elongation balance and fatigue characteristics |
| CN101245436A (en) * | 2007-02-16 | 2008-08-20 | 宝山钢铁股份有限公司 | High-strength toughness steel for continuous sucker rod and method for manufacturing same |
| CN101905392A (en) * | 2010-08-26 | 2010-12-08 | 宜昌猴王焊丝有限公司 | High-toughness low-alloy solid welding wire |
| CN102226252A (en) * | 2011-06-10 | 2011-10-26 | 钢铁研究总院 | High-toughness carburized bearing steel with ultra-long contact fatigue life and preparation method thereof |
| CN102251171A (en) * | 2010-05-19 | 2011-11-23 | 株式会社神户制钢所 | Thick steel plate with excellent fatigue characteristics |
| CN102286693A (en) * | 2011-07-28 | 2011-12-21 | 莱芜钢铁集团有限公司 | Thick ship plate steel and preparation method thereof |
| CN102864384A (en) * | 2012-08-31 | 2013-01-09 | 中国重汽集团济南动力有限公司 | High-strength automobile axle housing material and method for manufacturing axle housing |
| CN107419195A (en) * | 2017-08-04 | 2017-12-01 | 杰森能源技术有限公司 | A kind of deep well high pressure well high intensity high fatigue life coiled tubing and its manufacture method |
| WO2019092468A1 (en) * | 2017-11-08 | 2019-05-16 | Arcelormittal | A hot-dip coated steel sheet |
| CN111304531A (en) * | 2020-03-02 | 2020-06-19 | 马鞍山钢铁股份有限公司 | Hot-rolled H-shaped steel with yield strength of 550MPa and production method thereof |
-
2022
- 2022-03-03 CN CN202210207038.0A patent/CN114622137A/en active Pending
Patent Citations (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07150291A (en) * | 1993-12-01 | 1995-06-13 | Kobe Steel Ltd | High strength hot rolled steel sheet for working excellent in fatigue property |
| CN1847412A (en) * | 2005-04-12 | 2006-10-18 | 万向钱潮股份有限公司 | Annealing process of 20CrMnTi steel for cold extrusion |
| JP2007321201A (en) * | 2006-06-01 | 2007-12-13 | Kobe Steel Ltd | High-strength hot-rolled steel plate superior in strength-elongation balance and fatigue characteristics |
| CN101245436A (en) * | 2007-02-16 | 2008-08-20 | 宝山钢铁股份有限公司 | High-strength toughness steel for continuous sucker rod and method for manufacturing same |
| CN102251171A (en) * | 2010-05-19 | 2011-11-23 | 株式会社神户制钢所 | Thick steel plate with excellent fatigue characteristics |
| CN101905392A (en) * | 2010-08-26 | 2010-12-08 | 宜昌猴王焊丝有限公司 | High-toughness low-alloy solid welding wire |
| CN102226252A (en) * | 2011-06-10 | 2011-10-26 | 钢铁研究总院 | High-toughness carburized bearing steel with ultra-long contact fatigue life and preparation method thereof |
| CN102286693A (en) * | 2011-07-28 | 2011-12-21 | 莱芜钢铁集团有限公司 | Thick ship plate steel and preparation method thereof |
| CN102864384A (en) * | 2012-08-31 | 2013-01-09 | 中国重汽集团济南动力有限公司 | High-strength automobile axle housing material and method for manufacturing axle housing |
| CN107419195A (en) * | 2017-08-04 | 2017-12-01 | 杰森能源技术有限公司 | A kind of deep well high pressure well high intensity high fatigue life coiled tubing and its manufacture method |
| WO2019092468A1 (en) * | 2017-11-08 | 2019-05-16 | Arcelormittal | A hot-dip coated steel sheet |
| CN111304531A (en) * | 2020-03-02 | 2020-06-19 | 马鞍山钢铁股份有限公司 | Hot-rolled H-shaped steel with yield strength of 550MPa and production method thereof |
Non-Patent Citations (2)
| Title |
|---|
| 姚培友等: "20Cr2Ni4钢正火新工艺的研究", 《热处理技术与装备》 * |
| 王心明: "《工程压力容器设计与计算》", 31 August 1986, 国防工业出版社 * |
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