CN116904871A - HB 400-grade high-toughness wear-resistant steel and production method thereof - Google Patents
HB 400-grade high-toughness wear-resistant steel and production method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 46
- 239000010959 steel Substances 0.000 title claims abstract description 46
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 16
- 238000005496 tempering Methods 0.000 claims abstract description 26
- 238000001816 cooling Methods 0.000 claims abstract description 24
- 238000010791 quenching Methods 0.000 claims abstract description 17
- 230000000171 quenching effect Effects 0.000 claims abstract description 17
- 238000005266 casting Methods 0.000 claims abstract description 11
- 238000003723 Smelting Methods 0.000 claims abstract description 7
- 238000010438 heat treatment Methods 0.000 claims abstract description 5
- 150000001875 compounds Chemical class 0.000 claims abstract description 4
- 238000005520 cutting process Methods 0.000 claims abstract description 4
- 238000005098 hot rolling Methods 0.000 claims abstract description 4
- 238000000034 method Methods 0.000 claims description 13
- 230000008569 process Effects 0.000 claims description 12
- 238000005096 rolling process Methods 0.000 claims description 9
- 229910052698 phosphorus Inorganic materials 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 4
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 3
- 150000002910 rare earth metals Chemical class 0.000 claims description 3
- 229910001566 austenite Inorganic materials 0.000 description 13
- 230000000052 comparative effect Effects 0.000 description 6
- 239000013078 crystal Substances 0.000 description 5
- 229910000734 martensite Inorganic materials 0.000 description 5
- 229910052799 carbon Inorganic materials 0.000 description 4
- 238000007670 refining Methods 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 230000006911 nucleation Effects 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000004566 building material Substances 0.000 description 1
- 150000001721 carbon Chemical class 0.000 description 1
- 239000003245 coal Substances 0.000 description 1
- 238000013329 compounding Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000011089 mechanical engineering Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000005272 metallurgy Methods 0.000 description 1
- 230000005012 migration Effects 0.000 description 1
- 238000013508 migration Methods 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 230000009466 transformation 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B15/00—Arrangements for performing additional metal-working operations specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
-
- 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
- C21D11/00—Process control or regulation for heat treatments
-
- 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
- C21D11/00—Process control or regulation for heat treatments
- C21D11/005—Process control or regulation for heat treatments for cooling
-
- 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
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/06—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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B15/00—Arrangements for performing additional metal-working operations specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B2015/0057—Coiling the rolled product
-
- 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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
HB 400-grade high-toughness wear-resistant steel comprises the following components in percentage by weight: c:0.10 to 0.18 percent, mn:0.2 to 1.3 percent, P is less than or equal to 0.020 percent, S is less than or equal to 0.010 percent, als:0.03 to 0.06 percent, nb:0.010 to 0.02 percent, ti: 0.005-0.02%, si: less than or equal to 0.020 percent or B: less than or equal to 0.003 percent or the two are added in a compound way according to any proportion; the production method comprises the following steps: conventionally smelting and casting into blanks; heating a casting blank and then hot-rolling; continuously uncoiling and quenching after coiling; cooling at a high speed; tempering after transverse cutting according to a fixed length; naturally cooling to room temperature. The invention ensures that the hardness HB of the product is not lower than 400, the yield strength is not lower than 930MPa, the tensile strength is not lower than 1100MPa, the elongation is not lower than 10 percent, the impact energy at minus 40 ℃ is not lower than 50J, the components are simple, and the production cost can be reduced by at least 2 percent.
Description
Technical Field
The invention relates to wear-resistant steel for mechanical engineering and a production method thereof, in particular to HB 400-grade high-toughness wear-resistant steel suitable for being used in an environment of minus 40 ℃ and a production method thereof.
Background
The low-alloy high-strength wear-resistant steel is applied to mechanical equipment such as metallurgy, mines, building materials, railways, electric power, coal and the like, and with the deep advancement of important national strategies, the demand of downstream industries such as commercial vehicles, engineering machinery and the like for the wear-resistant steel is increased day by day, however, the low-temperature toughness of the current wear-resistant steel at the temperature of minus 40 ℃ can only reach the level of 10-20J, and the application requirements of low-temperature environments are difficult to meet.
As the wear-resistant steel mainly adopts structure reinforcement to ensure the structure and the performance, the martensite strength is high, the original austenite grains are coarse after quenching, so that the strength of the wear-resistant steel is generally up to 1200 MPa-1400 MPa, but the toughness after low-temperature tempering is poor, and the toughness is difficult to meet simultaneously.
The document of Chinese patent publication No. CN102605234A discloses a wear-resistant steel plate and a manufacturing method thereof, wherein the wear-resistant steel plate comprises the following components in percentage by weight: c:0.08-0.24%, si:0.10-0.30%, mn:0.70-1.70%, P: less than or equal to 0.050 percent, S: less than or equal to 0.030 percent, cr: less than or equal to 1.00 percent, mo: less than or equal to 0.60 percent, al:0.01-0.10%, B:0.0005-0.0040%, ti:0.005-0.06%, and satisfies: cr+Mo is more than or equal to 0.15 and less than or equal to 1.20%, al+Ti is more than or equal to 0.011% and less than or equal to 0.15%, and the balance is Fe and unavoidable impurities. The casting-rolling control-tempering heat treatment process is adopted for production, has excellent performance, is suitable for manufacturing equipment which is easy to wear in engineering machinery, has the defect that the low-temperature toughness of the equipment can only reach the level of 10-20J, and can generate the risk of cracking if the equipment is applied to a low-temperature environment of minus 40 ℃.
Therefore, the existing wear-resistant steel has the technical problems of poor low-temperature toughness, easiness in cracking and the like, so that components and processes are necessary to be redesigned, and the product quality and the production efficiency are improved.
Disclosure of Invention
The invention aims to overcome the defects existing in the prior art and provide HB 400-grade high-toughness wear-resistant steel produced by CSP, which has simple components and reduced production cost by at least 2 percent, on the premise of ensuring that the product hardness HB is not lower than 400, the yield strength is not lower than 930MPa, the tensile strength is not lower than 1100MPa and the elongation is not lower than 10 percent, and the impact energy at minus 40 ℃ is not lower than 50J.
Measures for achieving the above object:
the HB 400-grade high-toughness wear-resistant steel comprises the following components in percentage by weight: c:0.10 to 0.18 percent, mn:0.2 to 1.3 percent, P is less than or equal to 0.020 percent, S is less than or equal to 0.010 percent, als:0.03 to 0.06 percent, nb:0.010 to 0.02 percent, ti: 0.005-0.02%, si: less than or equal to 0.020 percent or B: less than or equal to 0.003 percent or the two are added in a compound way according to any proportion, and the balance is Fe and impurities.
Preferably: the weight percentage content of Si is 0.015-0.16%.
Preferably: the weight percentage content of Ti is 0.005-0.013%.
Preferably: the weight percentage content of Als is 0.035-0.05%.
Preferably: : the weight percentage content of the B is 0.001-0.0026 percent.
A production method of HB 400-grade high-toughness wear-resistant steel comprises the following steps:
1) Conventionally smelting and casting into blanks, wherein rare earth is added to modify inclusions in the smelting process;
controlling the thickness of the casting blank to be 40-80 mm;
2) Carrying out hot rolling after conventionally heating a casting blank, controlling the final rolling temperature FT7 to be 800-830 ℃ and the coiling temperature CT to be 550-580 ℃;
3) Continuously uncoiling after conventional coiling and quenching, wherein the quenching temperature is controlled to be 850-950 ℃, and the quenching time is controlled to be 5-10 minutes;
4) Cooling at a high speed, and cooling to 50-150 ℃ at a cooling speed of 50-100 ℃/s;
5) Tempering is carried out after the transverse cutting according to the fixed length, the tempering temperature is controlled to be 200-240 ℃, and the tempering time is controlled to be 30-100 min;
6) Naturally cooling to room temperature.
Preferably: the quenching temperature is 863-935 ℃.
Preferably: cooling to 57-138 ℃ at the cooling speed of 58-93 ℃/s.
Preferably: the tempering temperature is 205-233 ℃ and the tempering time is 36-75 min.
The action and mechanism of each element and main process in the invention
C: c is the cheapest element for improving the strength of the material, and the hardness and strength are improved with the increase of the carbon content, but the toughness and welding performance are reduced. Comprehensively considering that the weight percentage of C is 0.10 to 0.18 percent.
Si: si can reduce the diffusion rate of carbon in ferrite, promote ferrite formation, and also deteriorate the surface quality. In comprehensive consideration, the Si content is preferably 0 to 0.2% by weight.
Mn: mn can obviously reduce Ar1 temperature and austenite decomposition speed, improve supercooled austenite stability, promote austenite release stress, increase residual austenite content in a final structure, and improve cold bending performance, but if the Mn content is too high, tempering brittleness can be increased, serious center segregation is caused, and the Mn weight percentage is preferably 0.2-1.3% comprehensively considered.
Als: als can deoxidize in steel, reduce the content of inclusions, and also play a role in refining grains, and comprehensively consider that Als is 0.03-0.06%.
Nb: nb has extremely strong affinity with C, N in steel to form stable Nb (C, N) compound, is induced to separate out in the controlled rolling process, is dispersed and distributed along the austenite grain boundary, and can be used as nucleation points of phase transformation to effectively prevent recrystallization, improve ferrite nucleation rate, have remarkable effect on refining grains and be considered comprehensively, and the Nb weight percentage is preferably 0.010-0.02%.
Ti: ti can combine with N to generate stable TiN in the solidification process of steel, and can strongly block the migration of austenite grain boundaries, thereby refining austenite grains. Considering comprehensively, the Ti content is preferably 0.005-0.02% by weight.
B: the quenching degree can be greatly improved by adding a trace amount of B into the steel, but when B is too much, the B is easy to enrich in crystal boundaries, the crystal boundary bonding energy can be reduced, so that the steel plate is more prone to fracture along the crystal when being subjected to impact load, and the low-temperature impact energy of the steel plate is reduced, and therefore, the addition amount of B in the invention is less than or equal to 0.0003 percent.
P, S: p, S is a harmful impurity element in steel, P in steel is easy to form segregation in steel, toughness and welding performance of steel are reduced, S is easy to form plastic sulfide, layering is generated on a steel plate, and performance of the steel plate is deteriorated, so that the lower the P, S content is, the better, and the P, S content of steel is more than or equal to 0.005% and less than or equal to 0.020% and S is less than or equal to 0.010% comprehensively considered. The reason why the P content is not less than 0.005% is that the atmospheric corrosion resistance can be further improved by compounding Cu.
The invention controls the final rolling temperature FT7 at 800-830 ℃, which is because coarse grains are easy to be caused when the final rolling temperature is higher, and the invention is beneficial to grain refinement in the rolling process when the final rolling temperature is lower than 800 ℃,
mixed crystals are easy to be caused, and the final structure and performance are affected.
The invention controls the coiling temperature CT at 550-580 ℃, because the thickness of the steel coil is thinner, when the coiling temperature is lower than 550 ℃, the steel coil is difficult to resist thermal stress, the shape and the coil shape of the steel plate are deteriorated, when the coiling temperature is higher than 580 ℃, the cooling speed in the cooling stage is insufficient, austenite grains are coarse, and the performance of the finished product is also adversely affected.
The quenching temperature is controlled between 850 and 950 ℃, preferably between 863 and 935 ℃, because the steel plate cannot be fully austenitized when the quenching temperature is lower than 850 ℃, the steel plate can have mixed crystal structure, the structure and the performance uniformity of the finished steel plate are affected, and when the quenching temperature is higher than 950 ℃, the original austenite grains are coarse, the size of the lath is large after the lath is transformed into martensite, and the toughness is seriously affected.
The cooling speed is controlled to be 50-150 ℃ at 50-100 ℃/s, and the cooling speed is preferably controlled to be 57-138 ℃ at 58-93 ℃/s, because the austenite can be prevented from growing in the cooling process, and the austenite is quenched to a martensite region in the cooling process, so that a uniform and fine martensite structure is obtained. In addition, the residual austenite is stabilized when the temperature is cooled to 50-150 ℃, and the final toughness is improved.
The tempering temperature is controlled to be 200-240 ℃ and the tempering time is controlled to be 30-100 minutes, preferably the tempering temperature is controlled to be 205-233 ℃ and the tempering time is controlled to be 36-75 minutes, because when the tempering temperature is lower than 200 ℃ or the tempering time is lower than 30 minutes, the tempering effect is poor, the improvement capability on the plate shape and the internal stress is weak, when the tempering temperature is higher than 240 ℃ or the tempering time is higher than 100 minutes, supersaturated carbon in martensite is easy to precipitate, the solid solubility is reduced, the influence of strength and hardness is larger, and the risk of performance mismatch is larger.
Compared with the prior art, the invention ensures that the hardness HB of the product is not lower than 400, the yield strength is not lower than 930MPa, the tensile strength is not lower than 1100MPa, the elongation is not lower than 10 percent, the impact energy at minus 40 ℃ is not lower than 50J, the components are simple, and the production cost can be reduced by at least 2 percent.
Detailed Description
The present invention will be described in detail below:
table 1 is a listing of chemical components of each example and comparative example of the present invention;
table 2 is a list of the main process parameters for each example and comparative example of the present invention;
table 3 shows a list of performance test cases for each example of the present invention and comparative example.
The embodiments of the invention were produced according to the following steps
1) Conventionally smelting and casting into blanks, wherein rare earth is added to modify inclusions in the smelting process; controlling the thickness of the casting blank to be 40-80 mm;
2) Carrying out hot rolling after conventionally heating a casting blank, controlling the final rolling temperature FT7 to be 800-830 ℃ and the coiling temperature CT to be 550-580 ℃;
3) Continuously uncoiling after conventional coiling and quenching, wherein the quenching temperature is controlled to be 850-950 ℃, and the quenching time is controlled to be 5-10 minutes;
4) Cooling at a high speed, and cooling to 50-150 ℃ at a cooling speed of 50-100 ℃/s;
5) Tempering is carried out after the transverse cutting according to the fixed length, the tempering temperature is controlled to be 200-240 ℃, and the tempering time is controlled to be 30-100 min;
6) Naturally cooling to room temperature.
TABLE 1 list of chemical Components (wt%) of examples and comparative examples of the present invention
TABLE 2 list of the main process parameters for each example and comparative example of the present invention
TABLE 3 mechanical property test results list for each example and comparative example of the present invention
From table 3, it can be seen that the low-temperature toughness of the wear-resistant steel is essentially improved compared with the wear-resistant steel of the traditional process under the condition of no reduction of strength by technological innovation under the condition of simpler component design and lower alloy content, and the level of 1.5-2 times of the comparison technological performance is reached.
This embodiment is merely a best example and is not intended to limit the implementation of the technical solution of the present invention.
Claims (9)
1. The HB 400-grade high-toughness wear-resistant steel comprises the following components in percentage by weight: c:0.10 to 0.18 percent, mn:
0.2～1.3％，P≤0.020％，S≤0.010％，Als：0.03～0.06％，Nb：0.010～0.02％，Ti：
0.005-0.02%, si: less than or equal to 0.020 percent or B: less than or equal to 0.003 percent or the two are added in a compound way according to any proportion, and the balance is Fe and impurities.
2. The HB400 grade high toughness wear resistant steel of claim 1, wherein: the weight percentage content of Si is 0.015-0.16%.
3. The HB400 grade high toughness wear resistant steel of claim 1, wherein: the weight percentage content of Ti is 0.005-0.013%.
4. The HB400 grade high toughness wear resistant steel of claim 1, wherein: the weight percentage content of Als is 0.035-0.05%.
5. The HB400 grade high toughness wear resistant steel of claim 1, wherein: the weight percentage content of the B is 0.001-0.0026 percent.
6. A method of producing a HB400 grade high toughness wear resistant steel according to claim 1 comprising the steps of:
1) Conventionally smelting and casting into blanks, wherein rare earth is added to modify inclusions in the smelting process;
controlling the thickness of the casting blank to be 40-80 mm;
2) Carrying out hot rolling after conventionally heating a casting blank, controlling the final rolling temperature FT7 at 800-830 ℃ and the coiling temperature CT at 550-580 ℃;
3) Continuously uncoiling after conventional coiling and quenching, wherein the quenching temperature is controlled to be 850-950 ℃, and the quenching time is controlled to be 5-10 minutes;
4) Cooling at a high speed, and cooling to 50-150 ℃ at a cooling speed of 50-100 ℃/s;
5) Tempering is carried out after the transverse cutting according to the fixed length, the tempering temperature is controlled to be 200-240 ℃, and the tempering time is controlled to be 30-100 min;
6) Naturally cooling to room temperature.
7. The method for producing the HB400 grade high-toughness wear-resistant steel according to claim 6, wherein: the quenching temperature is 863-935 ℃.
8. The method for producing the HB400 grade high-toughness wear-resistant steel according to claim 6, wherein: cooling to 57-138 ℃ at the cooling speed of 58-93 ℃/s.
9. The method for producing the HB400 grade high-toughness wear-resistant steel according to claim 6, wherein: the tempering temperature is 205-233 ℃ and the tempering time is 36-75 min.
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| CN114934156A (en) * | 2022-03-30 | 2022-08-23 | 鞍钢股份有限公司 | Production method of high-strength and high-toughness hot continuous rolling thin steel plate with Brinell hardness of 450HBW |
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