AU2020467306A1 - Thick low-carbon-equivalent high-toughness wear-resistant steel plate and manufacturing method therefor - Google Patents
Thick low-carbon-equivalent high-toughness wear-resistant steel plate and manufacturing method therefor Download PDFInfo
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- 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
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- 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
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Abstract
A thick low-carbon-equivalent high-toughness wear-resistant steel plate and a manufacturing method therefor, relating to the technical field of steel production. The steel plate comprises the following chemical components by mass percentage: C: 0.15%-0.17%, Si: 0.20%-0.40%, Mn: 0.90%-1.10%, P≤0.012%, S≤0.002%, Cr: 0.60%-0.80%, Mo: 0.30%-0.50%, Ni: 0.50%-0.70%, Ti: 0.008%-0.020%, Nb≤0.050%, V≤0.020%, B: 0.0010%-0.0020%, Alt: 0.04%-0.07%, N≤0.0040%, H≤0.0002%, with the balance being Fe and inevitable impurities. Ceq≤0.60%, and Pcm≤0.32%. The mechanical properties of the steel plate are as follows: the yield strength is greater than or equal to 1000 MPa, the tensile strength is greater than or equal to 1100 MPa, the elongation is greater than or equal to 10%, the surface Brinell hardness is greater than 400 HB, the core Brinell hardness is greater than 330 HB, the -40℃
Description
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'iL
__ a a ~ Mn~090ao~110a Ps%.012%, S~cE0.002%, 0, __ C: 0.15a~~~~0.17~, Si: 0.20a 0.020o, Nb< Cr: 0.60ao~~0.80a, Mo: 0.30a~~~~0.50o, Ni: 0.50a Ti: a 0 a 50o, a 0 0.0020%, Alt: 0,04aa~0,07a, N$~0,0040a, H$~0,0002a, t@ZtFetUTP <o.o~oa~,B: 00010a a a a fl-u a 0. t~t[IAL 10 C Ceq~0.60o~ Pcm~. 320ao~VtKfvm flb ~iJLtT7J(9:J~JW~&t~> GOMPa, 1lOOMPa, 3~f 434k~10aa, flhiT~L~t#400HB, SfiT~L~t#330HB, 27J, L½t~ttF~LAL {' 42 VJ TTL~~80aO, %ist L
[00011 The present disclosure relates to the technical field of steel production, and specifically relates to a thick low-carbon-equivalent high-toughness wear-resistant steel plate and a manufacturing method therefor.
[0002] Wear-resistant steel is widely used in the manufacturing of mechanical equipment in the fields of engineering machinery and coal mining machinery that require high strength and high wear resistance, such as excavators, bulldozers, loaders, dump trucks, scraper conveyors, various grabs, stacker-reclaimers, conveying bending structures and the like. The steel plate used in these fields is required to not only have high strength and hardness to resist wear, but also have good low-temperature toughness and welding performance to extend the service life of the mechanical equipment.
[00031 Low-alloy wear-resistant steel usually has low and unstable impact toughness in the production, which leads to the easy fracture and poor wear resistance of the steel plate obtained under the impact conditions. In recent years, as the equipment manufactured is increasingly large scale and long-life, the demand for the thick low-alloy wear-resistant steel plate is increasing. At present, the high-toughness wear-resistant steel plate with the thickness greater than 60 mm at home and abroad generally has technical bottlenecks such as high carbon equivalent, high cracking risk and high alloy cost, with the reason that the steel plate usually has high alloy content to ensure high strength and hardness due to the large thickness.
[00041 The Chinese patent with the publication No. of CN 107299279 A discloses a 100 mm thick 410 HB wear-resistant steel plate and a manufacturing method therefor. Although the steel plate has large thickness, low carbon equivalent, and excellent low-temperature impact toughness, the core hardness is not evaluated. In addition to the surface hardness, some equipment in the field of engineering machinery requires that the core hardness of the steel plate is generally not less than % of the surface hardness.
[00051 The Chinese patent with the publication No. of CN 103146997 B discloses a low-alloy high-toughness wear-resistant steel plate and a manufacturing method therefor. Although the surface hardness is greater than 400 HB, and the impact energy at -40 °C is greater than 60 J, the thickness is less than or equal to 50 mm, which does not meet the requirements of large thickness. The core hardness of the steel plate is also not evaluated.
[00061 The Chinese patent with the publication No. of CN 109280850 A discloses an 80 mm thick high-toughness low-alloy wear-resistant steel plate and a manufacturing method therefor. Although the thickness is large, the impact energy at -40 °C is greater than 20 J, and the core hardness is not less than 80% of the surface hardness, the carbon equivalent calculated according to the chemical composition is more than 0.65, and the welding performance is poor.
[00071 To overcome the shortcomings in the prior art, the present disclosure provides a thick low carbon-equivalent high-toughness wear-resistant steel plate. The thick low-carbon-equivalent high-toughness wear-resistant steel plate manufactured has high strength, high hardness, and good low-temperature impact toughness. The core hardness is not less than 80% of the surface hardness.
[00081 To solve the above-mentioned technical problems, the present disclosure provides the thick low-carbon-equivalent high-toughness wear-resistant steel plate, which is composed of the following chemical composition in mass percentage: C: 0.15%-0.17%, Si: 0.20%-0.40%, Mn: 0.90%-1.10%, P< 0.012%, S < 0.002%, Cr: 0.60%-0.80%, Mo: 0.30%-0.50%,Ni: 0.50%-0.70%, Ti: 0.008%-0.020%, Nb 0.050%, V < 0.020%, B: 0.0010%-0.0020%, Alt: 0.04%-0.07%, N 0.0040%, H < 0.0002%, and a balance of Fe and inevitable impurities.
[00091 The technical effects are as follows: The steel plate manufactured by the present disclosure has the following mechanical properties: The yield strength is > 1000 MPa, the tensile strength is > 1100 MPa, the elongation is > 10%, the surface hardness is greater than 400 HB, the core hardness is greater than 330 HB, and the impact energy (AKV) at -40 °C is > 27 J, and the welding performance is good.
[00101 The technical solutions further limited by the present disclosure are as follows:
[00111 The thick low-carbon-equivalent high-toughness wear-resistant steel plate described above is composed of the following chemical composition in mass percentage: C: 0.15%, Si: 0.40%, Mn: 1.10%, P < 0.012%, S 0.002%, Cr: 0.60%, Mo: 0.50%, Ni: 0.60%, Ti: 0.015%, Nb 0.050%, V 0.020%, B: 0.0015%, Alt: 0.045%, N 0.0040%, H 0.0002%, and the balance of Fe and inevitable impurities.
[00121 The thick low-carbon-equivalent high-toughness wear-resistant steel plate described above is composed of the following chemical composition in mass percentage: C: 0.16%, Si: 0.30%, Mn: 1.00%, P 0.012%, S < 0.002%, Cr: 0.80%, Mo: 0.30%, Ni: 0.50%, Ti: 0.012%, Nb < 0.050%, V 0.020%, B: 0.0018%, Alt: 0.055%, N 0.0040%, H 0.0002%, and the balance of Fe and inevitable impurities.
[00131 The thick low-carbon-equivalent high-toughness wear-resistant steel plate described above is composed of the following chemical composition in mass percentage: C: 0.17%, Si:
0.25%, Mn: 0.90%, P50.012%, S < 0.0015%, Cr: 0.70%, Mo: 0.40%,Ni: 0.70%,Ti: 0.018%,Nb 0.050%, V 5 0.020%, B: 0.0020%, Alt: 0.065%, N 5 0.0040%, H 5 0.0002%, and the balance of Fe and inevitable impurities.
[0014] The thick low-carbon-equivalent high-toughness wear-resistant steel plate is described above, a thickness of a steel plate obtained is 70 mm.
[00151 The thick low-carbon-equivalent high-toughness wear-resistant steel plate is described above, a microstructure of the steel plate is tempered martensite, and a content of the tempered martensite in a core structure of the steel plate is greater than 50%.
[0016] The thick low-carbon-equivalent high-toughness wear-resistant steel plate is described above, Ceq is 5 0.60%, Pcm is 5 0.32%, a formula to calculate Ceq is = C + Mn/6 + (Cr + Mo
+ V)/5 + (Ni + Cu)/15, and a formula to calculate Pcm is = C + Si/30 + (Mn + Cr + Cu)/20 + Ni/60 + Mo/15 + V/10 + 5B.
[00171 Another object of the present disclosure is providing a method for manufacturing the thick low-carbon-equivalent high-toughness wear-resistant steel plate, comprising: hot metal desulfurization pretreatment --* converter smelting --* ladle furnace (LF) and Ruhrstahl Heraeus (RH) refining -* continuous casting --* a cast billet stacking for slow cooling --* the cast billet acceptance --* the cast billet heating-* dephosphorization -* rolling --* air-cooling -- flaw detection --* shot blasting --* quenching-* tempering --* straightening --* cutting and sampling mark jet printing --* inspection --* stocking. The method specifically comprises:
[00181 carrying out the continuous casting after molten steel smelted according to a required chemical composition ratio is performed with RH vacuum treatment, to obtain the cast billet with a thickness of 260 mm; after the continuous casting is completed, stacking the cast billet into a slow-cooling pit for the slow cooling more than or equal to 48 h;
[00191 heating the cast billet with a holding time of 234-312 min and a soaking time of 40-50 min, and then tapping at 1200-1220 °C; carrying out a two-stage weakly controlled rolling process after the cast billet is heated, wherein, a high-reduction rolling with a speed less than or equal to 1.75 m/s is adopted in a first stage, a reduction rate of the last pass is > 25%, and the thickness of the cast billet to be heated is controlled to be more than 1.40 times a thickness of a finished product; an initial rolling temperature and a final rolling temperature in a second stage are < 950 °C and 920-940 °C, respectively, to obtain a steel plate with a thickness of 70 mm, and then the steel plate is air-cooled to room temperature; and
[0020] carrying out an off-line heat treatment, wherein, the quenching is carried out at 900-920 °C with a heating rate of 1.55 0.1 min/mm and the holding time of 30-40 min, the tempering is carried out at 170-190 °C with the heating rate of 35-45 °C/h and the holding time of 470-490 min, and then the steel plate is air-cooled.
[00211 The method for manufacturing the thick low-carbon-equivalent high-toughness wear resistant steel plate is described above, a roller hearth furnace is adopted for the quenching, a roller velocity of a quencher is 0.04 m/s, a water pressure in a high-pressure section of the quencher is the maximum of the quencher, and the steel plate swings five times in a low-pressure section of the quencher, and then a car bottom furnace is adopted for the tempering.
[00221 The beneficial effects of the present disclosure are as follows:
[00231 (1) Under the condition of low carbon equivalent, reasonable composition design, and optimized rolling and heat treatment processes, the core hardness of the thick low-carbon equivalent high-toughness wear-resistant steel plate manufactured by the present disclosure is not less than 80% of the surface hardness. And the thick low-carbon-equivalent high-toughness wear resistant steel plate has good low-temperature impact toughness and good welding performance.
[00241 (2) The cast billet used in the manufacturing of the thick low-carbon-equivalent high toughness wear-resistant steel plate of the present disclosure is stacked in the slow-cooling pit for the sufficient slow cooling more than or equal to 48 h, to ensure the diffusion of the H content of the cast billet and effectively reduce the risk of cutting cracking.
[00251 (3) The present disclosure optimizes the quenching process of the thick low-carbon equivalent high-toughness wear-resistant steel plate to effectively improve the hardenability and ensure the core hardness.
[00261 (4) The manufacturing method of the present disclosure is simple and feasible. The manufacturing process is short, and the manufacturing efficiency is improved. Thus, the economic benefit is increased.
[00271 FIG. 1 shows a surface metallographic structure of a tempered steel plate in Example 1;
[00281 FIG. 2 shows a metallographic structure at 1/4 thickness of the tempered steel plate in Example 1; and
[00291 FIG. 3 shows the metallographic structure at 1/2 thickness of the tempered steel plate in Example 1.
[00301 Example 1
[0031] This example provides the thick low-carbon-equivalent high-toughness wear-resistant steel plate with the thickness of 70 mm, which is composed of the following chemical composition in mass percentage: C: 0.15%, Si: 0.40%, Mn: 1.10%, P: 0.008%, S: 0.002%, Cr: 0.60%, Mo: 0.50%, Ni: 0.60%, Ti: 0.015%, Nb: 0.003%, V: 0.004%, B: 0.0015%, Alt: 0.045%, N: 0.0035%,
H: 0.00015%, and the balance of Fe and inevitable impurities.
[00321 The manufacturing process includes: hot metal desulfurization pretreatment-- converter smelting-* ladle furnace (LF) and Ruhrstahl Heraeus (RH) refining -- continuous casting-* the cast billet stacking for slow cooling-- the cast billet acceptance- the cast billet heating dephosphorization -* rolling -* air-cooling-* flaw detection -* shot blasting -* quenching-* tempering --* straightening --* cutting and sampling -- mark jet printing --* inspection --* stocking. The manufacturing process is specifically as follows:
[00331 The continuous casting is carried out after the molten steel smelted according to a required chemical composition ratio is performed with the RH vacuum treatment, to obtain the cast billet with the thickness of 260 mm. After the continuous casting is completed, the cast billet is stacked into the slow-cooling pit to for the slow cooling 60 h.
[00341 Then, the cast billet is heated with the holding time of 240 min and the soaking time of 40 min, and then tapped at 1200 °C. The two-stage weakly controlled rolling process is carried out after the cast billet is heated. The high-reduction rolling with the speed of 1.5-1.75 m/s is adopted in the first stage, the reduction rate of the last pass is 25%, and the thickness of the cast billet to be heated is controlled to be more than 1.40 times that of the finished product. The initial rolling temperature and the final rolling temperature in the second stage are 950 °C and 925 °C, respectively, to obtain the steel plate with the thickness of 70 mm. Then, the steel plate is air cooled to room temperature.
[00351 Then, the off-line heat treatment is carried out. The roller hearth furnace is adopted for the quenching at 910 °C with the heating rate of 1.55 min/mm and the holding time of 35 min. The roller velocity of the quencher is 0.04 m/s, the water pressure in the high-pressure section of the quencher is the maximum of the quencher, and the steel plate swings five times in the low-pressure section of the quencher. The car bottom furnace is adopted for the tempering at 180 °C with the heating rate of 40 °C/h and the holding time of 480 min, and then the steel plate is air-cooled.
[0036] Example 2
[00371 This example provides the thick low-carbon-equivalent high-toughness wear-resistant steel plate with the thickness of 70 mm. The difference from Example 1 is that:
[00381 The thick low-carbon-equivalent high-toughness wear-resistant steel plate is composed of the following chemical composition in mass percentage: C: 0.16%, Si: 0.30%, Mn: 1.00%, P: 0.010%, S: 0.0016%, Cr: 0.80%, Mo: 0.30%, Ni: 0.50%, Ti: 0.012%, Nb: 0.003%, V: 0.005%, B: 0.0018%,Alt: 0.055%, N: 0.0032%, H: 0.00018%, and the balance of Fe and inevitable impurities.
[00391 The manufacturing process is specifically as follows:
[00401 The continuous casting is carried out after the molten steel smelted according to a required chemical composition ratio is performed with the RH vacuum treatment, to obtain the cast billet with the thickness of 260 mm. After the continuous casting is completed, the cast billet is stacked into the slow-cooling pit for the slow cooling 60 h.
[0041] Then, the cast billet is heated with the holding time of 270 min and the soaking time of 45 min, and then tapped at 1210 °C. The two-stage weakly controlled rolling process is carried out after the cast billet is heated. The high-reduction rolling with the speed of 1.5-1.75 m/s is adopted in the first stage, the reduction rate of the last pass is 25%, and the thickness of the cast billet to be heated is controlled to be more than 1.40 times that of the finished product. The initial rolling temperature and the final rolling temperature in the second stage are 940 °C and 920 °C, respectively, to obtain the steel plate with the thickness of 70 mm. Then, the steel plate is air cooled to room temperature.
[00421 Then, the off-line heat treatment is carried out. The roller hearth furnace is adopted for the quenching at 900 °C with the heating rate of 1.55 min/mm and the holding time of 40 min. The roller velocity of the quencher is 0.04 m/s, the water pressure in the high-pressure section of the quencher is the maximum of the quencher, and the steel plate swings five times in the low-pressure section of the quencher. The car bottom furnace is adopted for the tempering at 185 °C with the heating rate of 40 °C/h and the holding time of 490 min, and then the steel plate is air-cooled.
[00431 Example 3
[00441 This example provides the thick low-carbon-equivalent high-toughness wear-resistant steel plate with the thickness of 70 mm. The difference from Example 1 is that:
[00451 The thick low-carbon-equivalent high-toughness wear-resistant steel plate is composed of the following chemical composition in mass percentage: C: 0.17%, Si: 0.25%, Mn: 0.90%, P: 0.009%, S: 0.0015%, Cr: 0.70%, Mo: 0.40%, Ni: 0.70%, Ti: 0.018%, Nb: 0.003%, V: 0.005%, B: 0.0020%,Alt: 0.065%, N: 0.0030%, H: 0.00016%, and the balance of Fe and inevitable impurities.
[00461 The manufacturing process is specifically as follows:
[00471 The continuous casting is carried out after the molten steel smelted according to a required chemical composition ratio is performed with the RH vacuum treatment, to obtain the cast billet with the thickness of 260 mm. After the continuous casting is completed, the cast billet is stacked into the slow-cooling pit for the slow cooling 60 h.
[00481 Then, the cast billet is heated with the holding time of 300 min and the soaking time of 50 min, and then tapped at 1220 °C. The two-stage weakly controlled rolling process is carried out after the cast billet is heated. The high-reduction rolling with the speed of 1.5-1.75 m/s is adopted in the first stage, the reduction rate of the last pass is 25%, and the thickness of the cast billet to be heated is controlled to be more than 1.40 times that of the finished product. The initial rolling temperature and the final rolling temperature in the second stage are 950 °C and 935 °C, respectively, to obtain the steel plate with the thickness of 70 mm. Then, the steel plate is air- cooled to room temperature.
[00491 Then, the off-line heat treatment is carried out. The roller hearth furnace is adopted for the quenching at 920 °C with the heating rate of 1.55 min/mm and the holding time of 30 min. The roller velocity of the quencher is 0.04 m/s, the water pressure in the high-pressure section of the quencher is the maximum of the quencher, and the steel plate swings five times in the low-pressure section of the quencher. The car bottom furnace is adopted for the tempering at 190 °C with the heating rate of 40 °C/h and the holding time of 490 min, and then the steel plate is air-cooled.
[00501 The mechanical properties of the steel plate obtained in examples were tested. Specifically, the strength was determined by the tensile test method of metallic materials at room temperature of GB/T228-2002, the low-temperature impact toughness was determined by the Charpy V-notch impact test method of metallic materials of GB/T229-2007, and the hardness was determined by the method of GB/T2311-2009. The performance test results are shown in Table 1.
[00511 Table 1 Mechanical properties of the steel plate of examples
[00521
Yield Tensile Elongation Impact energy Surface Core Example strength/MPa strength/MPa A50/% at-40C hardness/HB hardness/HB stregth!~a trenthl~a A0/%(KV2)/J
1 1085 1378 14.5 36 426 351
2 1168 1318 15.5 33 429 346
3 1072 1300 14 46 421 333
[00531 From Table 1, the mechanical properties of the steel plate of the present disclosure are shown as follows: the yield strength is greater than 1000 MPa, the tensile strength is greater than 1100 MPa, the elongation is greater than 10%, the surface hardness is greater than 400 HB, the core hardness is greater than 330 HB, and the impact energy at - 40 °C is greater than 27 J. The steel plate of the present disclosure has good deformation resistance, wear resistance, and good low-temperature impact toughness.
[00541 It can be seen from Figs. 1-3 that the metallographic structure of the steel plate from the surface to the 1/4 thickness is tempered martensite, and the content of tempered martensite at the 1/2 thickness is more than 50%.
[0055] In addition to the above-mentioned examples, the present disclosure may also have other examples. All technical solutions formed by equivalent replacements or transformations shall fall within the protection scope of the present disclosure.
Claims (9)
1. A thick low-carbon-equivalent high-toughness wear-resistant steel plate, wherein, the thick low-carbon-equivalent high-toughness wear-resistant steel plate is composed of the following chemical composition in mass percentage: C: 0.15%-0.17%, Si: 0.20%-0.40%, Mn: 0.90%-1.10%, P < 0.012%, S < 0.002%, Cr: 0.60%-0.80%, Mo: 0.30%-0.50%, Ni: 0.50%-0.70%, Ti: 0.008% 0.020%, Nb < 0.050%, V < 0.020%, B: 0.0010%-0.0020%, Alt: 0.04%-0.07%, N < 0.0040%, H < 0.0002%, and a balance of Fe and inevitable impurities.
2. The thick low-carbon-equivalent high-toughness wear-resistant steel plate according to claim 1, wherein the thick low-carbon-equivalent high-toughness wear-resistant steel plate is composed of the following chemical composition in mass percentage: C: 0.15%, Si: 0.40%, Mn: 1.10%, P < 0.012%, S < 0.002%, Cr: 0.60%, Mo: 0.50%, Ni: 0.60%, Ti: 0.015%, Nb < 0.050%, V 0.020%, B: 0.0015%, Alt: 0.045%, N < 0.0040%, H < 0.0002%, and the balance of Fe and inevitable impurities.
3. The thick low-carbon-equivalent high-toughness wear-resistant steel plate according to claim 1, wherein the thick low-carbon-equivalent high-toughness wear-resistant steel plate is composed of the following chemical composition in mass percentage: C: 0.16%, Si: 0.30%, Mn: 1.00%, P < 0.012%, S < 0.002%, Cr: 0.80%, Mo: 0.30%, Ni: 0.50%, Ti: 0.012%, Nb < 0.050%, V 0.020%, B: 0.0018%, Alt: 0.055%, N < 0.0040%, H < 0.0002%, and the balance of Fe and inevitable impurities.
4. The thick low-carbon-equivalent high-toughness wear-resistant steel plate according to claim 1, wherein the thick low-carbon-equivalent high-toughness wear-resistant steel plate is composed of the following chemical composition in mass percentage: C: 0.17%, Si: 0.25%, Mn: 0.90%, P < 0.012%, S5 0.0015%, Cr: 0.70%, Mo: 0.40%, Ni: 0.70%, Ti: 0.018%, Nb < 0.050%, V < 0.020%, B: 0.0020%, Alt: 0.065%, N < 0.0040%, H < 0.0002%, and the balance of Fe and inevitable impurities.
5. The thick low-carbon-equivalent high-toughness wear-resistant steel plate according to claim 1, wherein a thickness of a steel plate obtained is 70 mm.
6. The thick low-carbon-equivalent high-toughness wear-resistant steel plate according to claim 1, wherein a microstructure of the steel plate is tempered martensite, and a content of the tempered martensite in a core structure of the steel plate is greater than 50%.
7. The thick low-carbon-equivalent high-toughness wear-resistant steel plate according to claim 1, wherein Ceq is 0.60%, and Pcm is 0.32%; a formula to calculate Ceq is = C + Mn/6 + (Cr + Mo + V )/5+ (Ni + Cu)/15, and a formula to calculate Pcm is = C + Si/30 + (Mn + Cr +
Cu)/20 + Ni/60 + Mo/15 + V/10 + 5B.
8. A method for manufacturing a thick low-carbon-equivalent high-toughness wear-resistant steel plate, comprising: hot metal desulfurization pretreatment-* converter smelting -* ladle furnace (LF) and Ruhrstahl Heraeus (RH) refining-* continuous casting --* a cast billet stacking for slow cooling -- the cast billet acceptance-* the cast billet heating-* dephosphorization rolling --* air-cooling --* flaw detection --* shot blasting --* quenching --* tempering straightening --* cutting and sampling --* mark jet printing --* inspection --* stocking, wherein, the method is applied to the manufacturing of the thick low-carbon-equivalent high-toughness wear resistant steel plate of any one of claims 1-7, and specifically comprises: carrying out the continuous casting after molten steel smelted according to a required chemical composition ratio is performed with RH vacuum treatment, to obtain the cast billet with a thickness of 260 mm; after the continuous casting is completed, stacking the cast billet into a slow-cooling pit for the slow cooling more than or equal to 48 h; heating the cast billet with a holding time of 234-312 min and a soaking time of 40-50 min, and then tapping at 1200-1220 °C; carrying out a two-stage weakly controlled rolling process after the cast billet is heated, wherein, a high-reduction rolling with a speed less than or equal to 1.75 m/s is adopted in a first stage, a reduction rate of the last pass is > 25%, and the thickness of the cast billet to be heated is controlled to be more than 1.40 times a thickness of a finished product; an initial rolling temperature and a final rolling temperature in a second stage are < 950 °C and 920-940 °C, respectively, to obtain a steel plate with a thickness of 70 mm, and then the steel plate is air-cooled to room temperature; and carrying out an off-line heat treatment, wherein, the quenching is carried out at 900-920 °C with a heating rate of 1.55 0.1 min/mm and the holding time of 30-40 min, the tempering is carried out at 170-190 °C with the heating rate of 35-45 °C/h and the holding time of 470-490 min, and then the steel plate is air-cooled.
9. The method for manufacturing the thick low-carbon-equivalent high-toughness wear resistant steel plate according to claim 8, wherein a roller hearth furnace is adopted for the quenching, a roller velocity of a quencher is 0.04 m/s, a water pressure in a high-pressure section of the quencher is the maximum of the quencher, and the steel plate swings five times in a low pressure section of the quencher, and then a car bottom furnace is adopted for the tempering.
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| CN202010951095.0 | 2020-09-11 | ||
| PCT/CN2020/133462 WO2022052335A1 (en) | 2020-09-11 | 2020-12-02 | Thick low-carbon-equivalent high-toughness wear-resistant steel plate and manufacturing method therefor |
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| CN115354138B (en) * | 2022-08-19 | 2023-11-21 | 河南中原特钢装备制造有限公司 | Heat treatment process for improving hardness uniformity of whole cross section of 20CrNiMo calender roll |
| CN115896623B (en) * | 2022-11-21 | 2024-08-27 | 包头钢铁（集团）有限责任公司 | Production method of structural steel plate for thick high-toughness yield strength 420 MPa-level wind power generation tower |
| CN115927967A (en) * | 2022-12-22 | 2023-04-07 | 美利林科技(攀枝花)有限公司 | High-toughness steel forging for ball mill and preparation process thereof |
| CN116356202A (en) * | 2023-03-09 | 2023-06-30 | 南京钢铁股份有限公司 | Ultra-wide quenched and tempered wear-resistant steel plate and manufacturing method thereof |
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| CN101775545B (en) * | 2009-01-14 | 2011-10-12 | 宝山钢铁股份有限公司 | Low-alloy high-strength high-toughness wear-resistant steel plate and manufacturing method thereof |
| CN101748333B (en) * | 2009-12-25 | 2012-02-01 | 舞阳钢铁有限责任公司 | Low-carbon-equivalent high-strength wear-resistant steel plate and production method thereof |
| KR20120071615A (en) * | 2010-12-23 | 2012-07-03 | 주식회사 포스코 | Wear resistant steel plate having excellent low-temperature toughness and weldability, and method for manufacturing the same |
| KR101322092B1 (en) * | 2013-08-01 | 2013-10-28 | 주식회사 포스코 | Wear Resistant Steel Plate Having Excellent Low-Temperature Toughness And Weldability, And Method For Manufacturing The Same |
| JP6135697B2 (en) * | 2014-03-04 | 2017-05-31 | Ｊｆｅスチール株式会社 | Abrasion-resistant steel sheet having excellent low-temperature toughness and low-temperature tempering embrittlement cracking properties and method for producing the same |
| JP2015193873A (en) * | 2014-03-31 | 2015-11-05 | Ｊｆｅスチール株式会社 | Thick steel plate excellent in abrasion resistance in corrosive environment |
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| CN105543669B (en) * | 2016-01-22 | 2017-06-23 | 山东钢铁股份有限公司 | A kind of think gauge and narrow hardness interval wear-resisting steel plate and preparation method thereof |
| CN106756544B (en) * | 2016-12-12 | 2019-06-04 | 南京钢铁股份有限公司 | A kind of production method of the big thickness Q690D high-strength steel of ultralow carbon equivalent |
| WO2018215600A1 (en) * | 2017-05-24 | 2018-11-29 | Tata Steel Uk Limited | High-strength, hot rolled abrasive wear resistant steel strip |
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| CN110643799B (en) * | 2019-10-08 | 2021-11-16 | 鞍钢股份有限公司 | Production method for uniformly improving hardness of core of wear-resistant steel plate |
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