CN116904870A - High-toughness wear-resistant medium-thickness steel plate suitable for environment of-40 ℃ and production method - Google Patents
High-toughness wear-resistant medium-thickness steel plate suitable for environment of-40 ℃ and production method Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 51
- 239000010959 steel Substances 0.000 title claims abstract description 51
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 16
- 238000005496 tempering Methods 0.000 claims abstract description 20
- 238000010791 quenching Methods 0.000 claims abstract description 16
- 230000000171 quenching effect Effects 0.000 claims abstract description 16
- 238000005266 casting Methods 0.000 claims abstract description 11
- 238000010438 heat treatment Methods 0.000 claims abstract description 11
- 238000001816 cooling Methods 0.000 claims abstract description 9
- 238000003723 Smelting Methods 0.000 claims abstract description 8
- 238000005520 cutting process Methods 0.000 claims abstract description 4
- 238000005096 rolling process Methods 0.000 claims description 31
- 238000000034 method Methods 0.000 claims description 9
- 230000008569 process Effects 0.000 claims description 9
- 230000009467 reduction Effects 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 4
- 150000002910 rare earth metals Chemical class 0.000 claims description 4
- 239000000203 mixture Substances 0.000 claims description 2
- 150000001875 compounds Chemical class 0.000 abstract description 3
- 238000005098 hot rolling Methods 0.000 abstract 1
- 229910001566 austenite Inorganic materials 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 229910052799 carbon Inorganic materials 0.000 description 4
- 229910000734 martensite Inorganic materials 0.000 description 4
- 238000007670 refining Methods 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910052757 nitrogen Inorganic materials 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
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-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
- 238000005336 cracking Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000005516 engineering 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
- 238000011056 performance test Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- 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)
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- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
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- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
A high-toughness wear-resistant medium-thickness steel plate suitable for being used in an environment of minus 40 ℃ comprises the following components in percentage by weight: c:0.17 to 0.25 percent, mn:1.7 to 2.1 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 of Ti: 0.010-0.02%, si is not more than 0.17%, cr is not more than 0.6%, or B is not more than 0.0003%, or a compound of two or more of them 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 has the advantages that the impact energy at the temperature of minus 40 ℃ is not lower than 40J on the premise that the width of the steel plate is 2000-2100 mm, the thickness is 15-25 mm, the yield strength of the product is not lower than 1140MPa, the tensile strength is not lower than 1260MPa, and the elongation is not lower than 10 percent, and the components are simple.
Description
Technical Field
The invention relates to wear-resistant steel for mechanical engineering and a production method thereof, in particular to a high-toughness wear-resistant medium-thickness steel plate 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 widely applied to mechanical equipment such as metallurgy, mines, building materials, railways, electric power, coal and the like, has severe use environment and has increasingly high quality requirements on strength, toughness, hardness and wear resistance. In particular low temperature toughness, has a profound effect on the risk of cracking during application. The traditional thin wear-resistant steel is optimized through rolling and cooling processes, and the lower coiling temperature is beneficial to refining microstructure, so that low-temperature toughness is improved. However, as thickness increases, the strength of thick gauge steel coils at lower coiling temperatures presents a greater challenge for coiling and crosscutting equipment. Therefore, for hot continuous rolling thick wear-resistant steel, the coiling temperature is usually higher, the original grains are coarse, the low-temperature toughness at-40 ℃ can only reach the level of 10-20J, and the low-temperature environment application requirement is difficult to meet in order to ensure the equipment safety.
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. Although the performance is excellent, the alloy is only suitable for manufacturing equipment which is easy to wear in engineering machinery, the high strength can deteriorate the low-temperature toughness, the temperature of 40 ℃ below zero is generally about 20J, the low-temperature environment of 40 ℃ below zero cannot be met, and the alloy is easy to crack.
As the wear-resistant steel mainly adopts structure reinforcement to ensure the structure and the performance, the strength of martensite is high, the original austenite grains are coarse after quenching, and 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.
Disclosure of Invention
The invention aims to overcome the defects in the prior art, and provides a high-toughness wear-resistant medium steel plate which is produced by CSP and is suitable for being used in the environment of-40 ℃ and has simple components and simple production method, wherein the width of the steel plate is 2000-2100 mm, the thickness of the steel plate is 15-25 mm, the yield strength of the steel plate is not lower than 1140MPa, the tensile strength of the steel plate is not lower than 1260MPa, the elongation of the steel plate is not lower than 10%.
Measures for achieving the above object:
a high-toughness wear-resistant medium-thickness steel plate suitable for being used in an environment of minus 40 ℃ comprises the following components in percentage by weight: c:0.17 to 0.25 percent, mn:1.7 to 2.1 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 of Ti: 0.010-0.02%, si not more than 0.17%, cr not more than 0.6%, or B not more than 0.0003%, or a mixture of two or more of them in any ratio, and the balance of Fe and unavoidable impurities.
Preferably: the weight percentage content of Mn is 1.75-1.90%.
A production method of a high-toughness wear-resistant medium-thickness steel plate suitable for being used in an environment of minus 40 ℃ comprises the following steps:
1) Conventionally smelting and casting into billets, wherein rare earth is added to modify inclusions according to 0.05-0.15 Kg/ton of steel in the smelting process;
2) Heating the casting blank, controlling the heating temperature of the casting blank to 1180-1230 ℃, and controlling the heating time of the high-temperature section to be not less than 60min;
3) Rough rolling: controlling the reduction rate of at least one of the first three passes to be not lower than 20%, and controlling the thickness of the plate blank at the end of rough rolling to be 40-80 mm;
4) Performing finish rolling, controlling the finish rolling temperature FT7 at 780-820 ℃, and controlling the total accumulated rolling reduction to be not lower than 60%, wherein the accumulated rolling reduction in the last three times is not lower than 40%;
5) Coiling, wherein the coiling temperature CT is controlled to be 700-750 ℃;
6) Continuously unwinding and quenching, controlling the quenching temperature to 790-830 ℃ and the quenching time to 5-10 minutes;
7) Tempering is carried out after the transverse cutting according to the fixed length, the tempering temperature is controlled to be 150-200 ℃, and the tempering time is controlled to be 10-30 min;
8) Naturally cooling to room temperature.
Preferably: the final rolling temperature FT7 is 785-815 ℃.
Preferably: the coiling temperature CT is 708-723 ℃.
Preferably: the quenching temperature is 796-823 ℃.
Preferably: the tempering temperature is 156-194 ℃.
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 0.17 to 0.25 percent;
mn: mn obviously reduces Ar1 temperature and austenite decomposition speed, improves supercooled austenite stability, promotes austenite release stress, increases residual austenite content in a final structure, and improves 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 0.5-2% 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%;
ti: ti has extremely strong affinity with C, N in steel to form stable Ti (C, N) compound, and is induced to separate out in the controlled rolling process, thereby effectively preventing recrystallization, and the functions of separating out and refining grains are obvious, and the weight percentage of Ti is preferably 0.010-0.020% comprehensively considered;
the Si is added to the alloy of the invention, wherein Si is not more than 0.17 percent or Cr is not more than 0.6 percent or B is not more than 0.0003 percent or a compound of two or more of the Si and the B according to any proportion, because Si can reduce the diffusion speed of carbon in ferrite, promote ferrite formation and also deteriorate the surface quality; cr can improve hardenability, can also improve tempering stability, reduce the cooling rate of the obtained martensite, but too high Cr reduces workability and weldability; b can greatly improve the hardenability, but when B is too much, the B is easy to enrich in the grain boundary, and can reduce the grain boundary bonding energy, so that the steel plate is more prone to fracture along the grain when being subjected to impact load, and the low-temperature impact energy of the steel plate is reduced, 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 less than or equal to 0.020% and the S is less than or equal to 0.010% comprehensively considered.
The temperature of the final rolling temperature FT7 is controlled between 780 and 820 ℃, preferably between 785 and 815 ℃, because coarse grains are easy to cause when the final rolling temperature is higher, grain refinement in the rolling process is facilitated when the final rolling temperature is lower, and mixed crystals are easy to cause when the final rolling temperature is lower than 780 ℃, so that the final structure and the performance are influenced.
The present invention controls the coiling temperature CT at 708-723 c, preferably 708-723 c, because the coil thickness is thin, it is difficult to resist thermal stress when the coiling temperature is lower than 708 c, deteriorating the shape and coil shape of the steel sheet, and when the coiling temperature is higher than 723 c, the cooling rate in the cooling stage is insufficient, austenite grains are coarse, and the properties of the finished product are adversely affected.
The quenching temperature is controlled between 790 and 830 ℃, preferably between 796 and 823 ℃, because when the quenching temperature is lower than 796 ℃, the steel plate cannot be completely austenitized, mixed crystal structures can appear on the steel plate, the structure and performance uniformity of the finished steel plate are affected, when the quenching temperature is higher than 823 ℃, the original austenite grains are coarse, the size of the lath is large after the original austenite grains are converted into martensite, and the toughness is seriously affected.
The tempering temperature is controlled to be 150-200 ℃, preferably 156-194 ℃, because the tempering effect is poor when the tempering temperature is lower than 156 ℃, the improvement capability on the plate shape and the internal stress is weak, and supersaturated carbon in martensite is easy to precipitate when the tempering temperature is higher than 194 ℃, 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 product yield strength is not lower than 1140MPa, the tensile strength is not lower than 1260MPa and the elongation is not lower than 10 percent under the premise that the width of the steel plate is 2000-2100 mm and the thickness is 15-25 mm, and the impact energy at minus 40 ℃ is not lower than 40J, so that the low-temperature environment is not cracked when in use; solves the difficult problem that the traditional hot continuous rolling production line is difficult to coil and transversely cut; under the condition of high-temperature coiling, the plate shape quality of the hot rolled coil is obviously improved; the components are simple.
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 billets, wherein rare earth is added to modify inclusions according to 0.05-0.15 Kg/ton of steel in the smelting process;
2) Heating the casting blank, controlling the heating temperature of the casting blank to 1180-1230 ℃, and controlling the heating time of the high-temperature section to be not less than 60min;
3) Rough rolling: controlling the reduction rate of at least one of the first three passes to be not lower than 20%, and controlling the thickness of the plate blank at the end of rough rolling to be 40-80 mm;
4) Performing finish rolling, controlling the finish rolling temperature FT7 at 780-820 ℃, and controlling the total accumulated rolling reduction to be not lower than 60%, wherein the accumulated rolling reduction in the last three times is not lower than 40%;
5) Coiling, wherein the coiling temperature CT is controlled to be 700-750 ℃;
6) Continuously unwinding and quenching, controlling the quenching temperature to 790-830 ℃ and the quenching time to 5-10 minutes;
7) Tempering is carried out after the transverse cutting according to the fixed length, the tempering temperature is controlled to be 150-200 ℃, and the tempering time is controlled to be 10-30 min;
8) Naturally cooling to room temperature.
Description:
adding rare earth into 0.05-0.15 Kg/ton steel in the smelting process to modify inclusions;
and the thickness of the plate blank is 40-80 mm at the end of rough rolling.
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 with wide and thick specifications is essentially improved compared with that of the wear-resistant steel with traditional technology under the condition that the component design is simpler and the alloy content is lower through technological innovation, 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 (7)
1. A high-toughness wear-resistant medium-thickness steel plate suitable for being used in an environment of minus 40 ℃ comprises the following components in percentage by weight: c:
0.17～0.25％，Mn：1.7～2.1％，P≤0.020％，S≤0.010％，Als：0.03～0.06％，Ti：
0.010-0.02%, si not more than 0.3%, cr not more than 0.6%, or B not more than 0.0003%, or a mixture of two or more of them in any ratio, and the balance Fe and unavoidable impurities.
2. A high toughness wear resistant medium thickness steel plate suitable for use in an environment of-40 ℃ as claimed in claim 1, wherein: the weight percentage content of Mn is 1.75-1.90%.
3. The method for producing a high-toughness wear-resistant medium steel plate suitable for use in an environment of-40 ℃ as claimed in claim 1, comprising the steps of:
1) Conventionally smelting and casting into billets, wherein rare earth is added to modify inclusions according to 0.05-0.15 Kg/ton of steel in the smelting process;
2) Heating the casting blank, controlling the heating temperature of the casting blank to 1180-1230 ℃, and controlling the heating time of the high-temperature section to be not less than 60min;
3) Rough rolling: controlling the reduction rate of at least one of the first three passes to be not lower than 20%, and controlling the thickness of the plate blank at the end of rough rolling to be 40-80 mm;
4) Performing finish rolling, controlling the finish rolling temperature FT7 at 780-820 ℃, and controlling the total accumulated rolling reduction to be not lower than 60%, wherein the accumulated rolling reduction in the last three times is not lower than 40%;
5) Coiling, wherein the coiling temperature CT is controlled to be 700-750 ℃;
6) Continuously unwinding and quenching, controlling the quenching temperature to 790-830 ℃ and the quenching time to 5-10 minutes;
7) Tempering is carried out after the transverse cutting according to the fixed length, the tempering temperature is controlled to be 150-200 ℃, and the tempering time is controlled to be 10-30 min;
8) Naturally cooling to room temperature.
4. A method for producing a high-toughness wear-resistant medium-thickness steel plate suitable for use in an environment of-40 ℃ as claimed in claim 3, wherein: the final rolling temperature FT7 is 785-815 ℃.
5. A method for producing a high-toughness wear-resistant medium-thickness steel plate suitable for use in an environment of-40 ℃ as claimed in claim 3, wherein: the coiling temperature CT is 708-723 ℃.
6. A method for producing a high-toughness wear-resistant medium-thickness steel plate suitable for use in an environment of-40 ℃ as claimed in claim 3, wherein: the quenching temperature is 796-823 ℃.
7. A method for producing a high-toughness wear-resistant medium-thickness steel plate suitable for use in an environment of-40 ℃ as claimed in claim 3, wherein: the tempering temperature is 156-194 ℃.
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|---|---|---|---|---|
| CN101691640A (en) * | 2009-09-01 | 2010-04-07 | 东北大学 | High strength low alloy wear resistance steel plate and preparation method thereof |
| CN102644030A (en) * | 2012-04-23 | 2012-08-22 | 武汉钢铁(集团)公司 | Cryogenic steel of which yield strength is 800 MPa class and production method thereof |
| CN111593264A (en) * | 2020-06-28 | 2020-08-28 | 武汉钢铁有限公司 | Tempering-free wear-resistant hot-rolled strip steel and production method thereof |
| CN116254480A (en) * | 2023-03-06 | 2023-06-13 | 皖西学院 | V-Ti-containing wear-resistant steel with hardness of HB 550-600 and production method thereof |
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- 2023-08-07 CN CN202310984641.4A patent/CN116904870A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101691640A (en) * | 2009-09-01 | 2010-04-07 | 东北大学 | High strength low alloy wear resistance steel plate and preparation method thereof |
| CN102644030A (en) * | 2012-04-23 | 2012-08-22 | 武汉钢铁(集团)公司 | Cryogenic steel of which yield strength is 800 MPa class and production method thereof |
| CN111593264A (en) * | 2020-06-28 | 2020-08-28 | 武汉钢铁有限公司 | Tempering-free wear-resistant hot-rolled strip steel and production method thereof |
| CN116254480A (en) * | 2023-03-06 | 2023-06-13 | 皖西学院 | V-Ti-containing wear-resistant steel with hardness of HB 550-600 and production method thereof |
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