AU2018387506A1 - High-grade low-alloy wear-resistant steel plate having brookfield hardness of greater than 550 HB and manufacturing method - Google Patents
High-grade low-alloy wear-resistant steel plate having brookfield hardness of greater than 550 HB and manufacturing method Download PDFInfo
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- 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
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- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- 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
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- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- 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
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- 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
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- 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
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- 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
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- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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Abstract
A low-alloy wear-resistant steel sheet having a Brookfield hardness of greater than 550 HB, comprising the following components in percentage by weight: 0.33-0.41% C, 0.50-0.60% Si, 0.30-0.80% Mn, less than or equal to 0.012% P, less than or equal to 0.003% S, 0.30-1.00% Cr, 0.20-0.60% Mo, 0.80-1.20% Ni, 0.008-0.030% Ti, 0.015-0.050% Nb, 0.080-0.150% V, 0.0008-0.0025% B, less than or equal to 0.0040% N, less than or equal to 0.0025% O, and the balance of Fe and inevitable impurities. The steel plate is designed with a medium to high level of carbon component and an alloying component. By using mutual synergy of alloying elements such as carbon, manganese, chromium, nickel, molybdenum, copper and the like and micro-alloying elements such as niobium, titanium, vanadium and the like supplemented by a method of controlled rolling and off-line heat treatment, the obtained steel plate has a Brookfield hardness of more than 550 HB and a low temperature impact toughness of greater than or equal to 20 J at -20 °C.
Description
High-Grade Low-Alloy Wear-Resistant Steel Plates with Brinell Hardness of Greater Than 550HB and Manufacturing Method Thereof
The present invention relates to the field of manufacturing of wear-resistant steel, specifically to high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB and manufacturing method thereof.
Compared with conventional wear-resistant cast steel, low-alloy wear-resistant steel plates have good comprehensive properties such as low alloy content, high low temperature impact toughness and bendable forming and the advantages such as flexible and convenient production and low production cost. They are widely used to manufacture mechanical equipment which is in poor working conditions and shall have high strength and hardness and desirable wear resistance in the sectors of engineering, mining, construction, agriculture, cement, port, electric power and metallurgy, such as bulldozers, loaders, excavators, dumpers, ball mills and various kinds of mining machinery, grab buckets, stacker-reclaimers and conveying bending structures. Such components generally work in a very harsh environment with alternate drying and wetting and it is difficult to replace them, so the steel plates shall have high strength and hardness, excellent wear and corrosion resistance, as well as good welding performance to ensure a higher service life of the equipment.
At present, there have been many patent reports on low-alloy wear-resistant steel, but the steel is in a low grade, has unsatisfactory hardness, toughness, plasticity and formability and poor welding performance and does not simultaneously possess excellent wear resistance and corrosion resistance, so it is difficult to meet the equipment manufacturing requirements for large scale, lightweight and long life. Particularly, low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB have not been disclosed in the prior art.
The technical problem that the present invention intends to solve is to provide high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB and manufacturing method thereof to address the defects existing in the prior art. The present invention adopts a composition design of medium-high carbon and alloying and obtains high-grade steel plates with Brinell hardness of greater than 550HB and -20°C low temperature impact toughness of not smaller than 20J through mutual cooperation and interaction of C, Mn, Cr, Ni, Co, Cu and other alloy elements and Nb, Ti, V and other microalloy elements and under the assistance of the methods of controlled rolling and off-line heat treatment. In addition to very high wear resistance, the obtained steel plates also have desirable corrosion resistance.
The present invention adopts the following technical solution to solve the foregoing technical problem:
High-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB, composed of the following components in weight percentage: C:0.33-0.41%, Si:0.50-0.60%, Mn:0.30-0.80%, P<0.012%, S<0.003%, Cr:0.30-1.00%, Mo:0.20-0.60%, Ni:0.80-1.20%, Ti:0.008-0.030%, Nb:0.015-0.050%, V:0.080-0.150%, B:0.0008-0.0025%, N<0.0040%, 0<0.0025%, and the rest being Fe and unavoidable impurities.
A manufacturing method of the high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB provided by the present invention, comprising the following flow: molten iron desulfurization pretreatment - converter smelting - LF + RH refining - continuous casting or die casting - cast billet hot charging - cast billet heating dephosphorization - rolling - controlled cooling or air cooling - flaw detection - shot blasting quenching - tempering - straightening - cutting - sampling - spray printing of identification inspection - warehousing; the cast billets or steel billets are heated at 1,180-1,220°C and then rolled in the austenite recrystallization region and non-recrystallization region respectively; the rolling requirements in the recrystallization region include pass reduction rate >12%, and finish rolling temperature >980°C; the rolling requirements in the non-recrystallization region include accumulated reduction rate >50%, initial rolling temperature <950°C, and finish rolling temperature >800°C; after rolling, temperature is reduced to room temperature by means of controlled cooling or air cooling, and then off-line heat treatment is performed with the quenching temperature at 820-930°C and the tempering temperature at 100-250°C.
The present invention further delimits the following technical solution:
In the foregoing high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB, the content of martensite in the structure is greater than 95%. The structure obtained in the present invention is principally martensite structure, and wear resistance is improved mainly relying on the high hardness and desirable toughness of martensite.
Of the foregoing high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB, the tensile strength is greater than 1900MPa, the hardness is greater than 570HBW, and the -20°C low temperature impact toughness is not smaller than 20J.
In the manufacturing method of the foregoing high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB, the cast billets of continuous casting are 150-300mm thick.
Owing to the compound addition of various alloy elements such as Cr, Ni and Co in the present invention, the obtained steel plates have both very high wear resistance and desirable corrosion resistance. The effect of each element is as follows:
C: Carbon is the most critical element for wear-resistant steel plates to obtain high strength and hardness. In order to obtain steel plates with martensite accounting for 95% or more of the structure and Brinell hardness of 570-630HB, carbon is the most important element. Further, carbon can significantly improve the hardenability of the steel plates. However, the increase of carbon will reduce the toughness, plasticity and welding performance of the steel plates. Therefore, in order that the steel plates have not only high hardness but also certain toughness, plasticity and welding performance, in comprehensive consideration, the content of carbon in the present invention is 0.33-0.41%.
Si: Silicon shows an effect of solution strengthening in steel, and its solubility in austenite is large. Increasing silicon content helps to improve the strength and hardness of steel and can improve the stability of austenite, but too high silicon content will lead to decrease of the toughness of the steel and the steel plates with high silicon content will have high viscosity of scale when being heated, causing difficulty in removing the scale after discharge from the furnace, and resulting in serious red scale on the surface of the rolled steel plates and poor surface quality. Further, high silicon content is not conducive to the welding performance of the steel plates. In comprehensive consideration of the effects of silicon element in various aspects, the content of silicon in the present invention is 0.50-0.60%.
Mn: Manganese can expand the austenite region and stabilize the austenite structure. Its ability is second only to alloy element nickel. It is a cheap element that stabilizes austenite and strengthens alloy. Meanwhile, manganese can enhance the hardenability of steel and reduce the critical cooling rate formed by martensite, but high manganese content makes the steel plates have a tendency of grain coarsening and increases the tempering brittleness sensitivity of the steel and may cause segregation and cracks in the billets and reduce the performance of the steel plates. The present invention combines the control of carbon and sulfur and controls the content of manganese at 0.30-0.80%.
S & P: Sulfur is liable to binding to manganese in steel to form sulfided inclusions, which are especially detrimental to the transverse plasticity and toughness of the steel, so the sulfur content should be as low as possible. Phosphorus is also a harmful element in steel, which seriously damages the plasticity and toughness of steel plates. For the present invention, sulfur and phosphorus are both inevitable impurity elements, and should be as low as possible. Considering the actual steelmaking level of steel mills, the present invention requires P < 0.012%, S < 0.003%.
Cr: Chromium can reduce the critical cooling rate and improve the hardenability of steel. Chromium can form various carbides such as (Fe, Cr)3C, (Fe, Cr)7C3 and (Fe, Cr)23C7 in steel to improve strength and hardness. Chromium can prevent or slow down the precipitation and aggregation of carbides during tempering, which can improve the tempering stability of steel. In the present invention, the content of chromium should be controlled at 0 .3 0 - 1 .0 0 %.
Co: Molybdenum can remarkably refine grains and improve strength and toughness. Molybdenum can reduce the temper brittleness of steel, and at the same time, very fine carbides can be precipitated during tempering, which significantly strengthen the steel matrix. Since molybdenum is a very expensive strategic alloy element, not more than 0.60% molybdenum can be added in the present invention. In the present invention, the content of molybdenum is 0.20-0.60%.
Ni: Nickel is an element that stabilizes austenite. Adding nickel to quenched and tempered steel can greatly improve the toughness of the steel, the low temperature toughness in particular. In the present invention, in order to ensure very high strength and hardness, high carbon content will be adopted in the alloy design, which will make the toughness and plasticity of the steel plates very poor. In order to ensure that the steel plates have high strength and hardness, and meanwhile have certain toughness and plasticity, and considering that nickel is a precious alloy element, the content of nickel in the present invention is 0.80-1.20%.
Ti: Titanium is a strong carbide forming element. The addition of a trace amount of titanium in steel helps to fix the nitrogen in the steel, and the formed TiN can make the austenite grains grow abnormally when the billets are heated, and refine the original austenite grain size. The content of titanium in the present invention is controlled at 0.008-0.030%.
Nb: Niobium in steel can stop recrystallization and hinder the growth of recrystallized grains, and raise the strength. At the same time, niobium can strongly form niobium carbides and nitrides in steel, thereby influencing the performance of the steel. Further, niobium can refine the grains and reduce the overheating sensitivity and temper brittleness of the steel. The content of niobium in the present invention is controlled at 0.015-0.050%.
B: Boron is an element of hardenability, which plays an important role in improving the hardenability of steel plates, especially thick steel plates. The addition of a small amount of boron in steel can remarkably increase the hardenability of the steel plates. Further, boron resources are rich and the price is cheap, and adding a small amount of boron can significantly reduce the addition of precious alloy elements such as manganese, nickel, chromium, and molybdenum. However, too much boron will increase the segregation of grain boundaries, thereby reducing the toughness and plasticity of steel materials. In the present invention, the content of boron is 0.0008-0.0025%.
The purpose of converter blowing and vacuum treatment is to ensure the basic composition requirements of the molten steel, remove harmful gases such as oxygen and hydrogen from the steel and add necessary alloying elements such as manganese and titanium to regulate the alloying elements.
Beneficial effects of the present invention: 1. The steel plates obtained in the present invention have very high hardness, greater than 570HB. 2. The present invention adopts a production method of hot rolling and off-line heat treatment. The production process is simple 3. The structure obtained in the present invention is mainly martensite structure, and the wear resistance is improved mainly relying on the high hardness and desirable toughness of martensite. 4. The wear-resistant steel plates obtained in the present invention have desirable low temperature impact toughness and cold roll forming performance and their -20°C low temperature impact toughness is >20J. 5. In addition to excellent wear resistance, the steel plates obtained in the present invention also have desirable corrosion resistance.
Embodiment 1
This embodiment provides high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB, composed of the following components in weight percentage: C:0.41%, Si:0.50%, Mn:0.56%, P<0.012%, S<0.003%, Cr:0.65%, Mo:0.36%, Ni:1.20%, Ti:0.008-0.030%, Nb:0.015-0.050%, V:0.080-0.150%, B:0.0008-0.0025%, N<0.0040%, 0<0.0025%, and the rest being Fe and unavoidable impurities.
This embodiment provides a manufacturing method of high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB: The molten steel obtained after smelting at the foregoing ratio is degassed under vacuum and then continuously cast, with the continuously cast billets being 150mm thick, the steel billets are heated to 1,180°C of furnace temperature, and maintained at this temperature for 180min, then discharged and rolled in the austenite recrystallization region and non-recrystallization region respectively, with the finish rolling temperature in the recrystallization region at 1,025°C, the finish rolling temperature in the non-recrystallization region at 910°C, and the final rolling thickness of steel plates at 12mm. After rolling, the steel plates are cooled in the air to room temperature, and then quenching and tempering treatment is performed with the quenching temperature at 880°C, and the tempering temperature at 170°C.
Embodiment 2
This embodiment provides high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB, composed of the following components in weight percentage: C:0.33%, Si:0.52%, Mn:0.80%, P<0.012%, S<0.003%, Cr:0.68%, Mo:0.60%, Ni:0.95%, Ti:0.008-0.030%, Nb:0.015-0.050%, V:0.080-0.150%, B:0.0008-0.0025%, N<0.0040%, 0<0.0025%, and the rest being Fe and unavoidable impurities.
This embodiment provides a manufacturing method of high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB: The molten steel obtained after smelting at the foregoing ratio is degassed under vacuum and then continuously cast, with the continuously cast billets being 220mm thick, the steel billets are heated to 1,200°C of furnace temperature, and maintained at this temperature for 200min, then discharged and rolled in the austenite recrystallization region and non-recrystallization region respectively, with the finish rolling temperature in the recrystallization region at 1,030°C, the finish rolling temperature in the non-recrystallization region at 850°C, and the final rolling thickness of steel plates at 40mm. After rolling, the steel plates are cooled in the air to room temperature, and then quenching and tempering treatment is performed with the quenching temperature at 920°C, and the tempering temperature at 250C.
Embodiment 3
This embodiment provides high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB, composed of the following components in weight percentage: C:0.40%, Si:0.51%, Mn:0.64%, P<0.012%, S<0.003%, Cr:1.00%, Mo:0.42%, Ni:0.80%, Ti:0.008-0.030%, Nb:0.015-0.050%, V:0.080-0.150%, B:0.0008-0.0025%, N<0.0040%, 0<0.0025%, and the rest being Fe and unavoidable impurities.
This embodiment provides a manufacturing method of high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB: The molten steel obtained after smelting at the foregoing ratio is degassed under vacuum and then continuously cast, with the continuously cast billets being 260mm thick, the steel billets are heated to 1,2200 C of furnace temperature, and maintained at this temperature for 220min, then discharged and rolled in the austenite recrystallization region and non-recrystallization region respectively, with the finish rolling temperature in the recrystallization region at 1,040°C, the finish rolling temperature in the non-recrystallization region at 890°C, and the final rolling thickness of steel plates at 25mm. After rolling, the steel plates are cooled in the air to room temperature, and then quenching and tempering treatment is performed with the quenching temperature at 930°C, and the tempering temperature at 1800 C.
Embodiment 4
This embodiment provides high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB, composed of the following components in weight percentage: C:0.38%, Si:0.60%, Mn:0.30%, P<0.012%, S<0.003%, Cr:0.30%, Mo:0.20%, Ni:0.50%, Ti:0.008-0.030%, Nb:0.015-0.050%, V:0.080-0.150%, B:0.0008-0.0025%, N<0.0040%, 0<0.0025%, and the rest being Fe and unavoidable impurities.
This embodiment provides a manufacturing method of high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB: The molten steel obtained after smelting at the foregoing ratio is degassed under vacuum and then continuously cast, with the continuously cast billets being 260mm thick, the steel billets are heated to 1,1800 C of furnace temperature, and maintained at this temperature for 180min, then discharged and rolled in the austenite recrystallization region and non-recrystallization region respectively, with the finish rolling temperature in the recrystallization region at 9800 C, the finish rolling temperature in the non-recrystallization region at 830C, and the final rolling thickness of steel plates at 25mm. After rolling, the steel plates are cooled in the air to room temperature, and then quenching and tempering treatment is performed with the quenching temperature at 820 0C, and the tempering temperature at100°C.
The mechanical properties of the steel plates in the embodiments were tested. Among them, strength was determined according to the method specified in GB/T228-2002 Metallic Materials-Tensile Testing at Ambient Temperature, low temperature impact toughness was determined according to GB/T 229-2007 Metallic Materials - Charpy Pendulum Impact Test Method, and hardness was determined by the method specified in GB/T231.1-2009. The obtained results area shown in Table 2.
Table 2 Mechanical properties of the steel plates provided by the present invention
Embodiment Tensile Impact energy at Elongation Hardness/HB strength/MPa -20 0 C KV2/J A50/% 1 1910 25 9.4 612
2 1750 35 10.6 558
3 2040 25 9.8 593
4 1880 28 9.1 588
Table 2 shows that the Brinell hardness of the wear-resistant steel provided by the present invention is greater than 550HB, the tensile strength is greater than 1,800MPa, the elongation is greater than 8%, and the impact energy at -20 0C is greater than 27J. It can be seen that the wear-resistant steel that the present invention relates to has desirable deformation resistance and wear resistance and good low temperature impact toughness.
In addition to the foregoing embodiments, the present invention may have other implementation manners. All the technical solutions formed from adoption of identical replacements or equivalent changes are within the scope of protection required by the present invention.
Claims (9)
1. High-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB, wherein the steel plates are composed of the following components in weight percentage: C:0.33-0.41%, Si:0.50-0.60%, Mn:0.30-0.80%, P<0.012%, S<0.003%, Cr:0.30-1.00%, Mo:0.20-0.60%, Ni:0.80-1.20%, Ti:0.008-0.030%, Nb:0.015-0.050%, V:0.080-0.150%, B:0.0008-0.0025%, N<0.0040%, 0<0.0025%, and the rest being Fe and unavoidable impurities.
2. The high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB according to claim 1, wherein in the steel plates, the content of martensite in the structure is greater than 95%.
3. The high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB according to claim 1, wherein the tensile strength of the steel plates is greater than 1,900MPa, the hardness is greater than 570HBW and the -20°C low temperature impact toughness is not smaller than 20J.
4. The high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB according to claim 1, wherein the steel plates are composed of the following components in weight percentage: C:0.41%, Si:0.50%, Mn:0.56%, P<0.012%, S<0.003%, Cr:0.65%, Mo:0.36%, Ni:1.20%, Ti:0.008-0.030%, Nb:0.015-0.050%, V:0.080-0.150%, B:0.0008-0.0025%, N<0.0040%, 0<0.0025%, and the rest being Fe and unavoidable impurities.
5. The high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB according to claim 1, wherein the steel plates are composed of the following components in weight percentage: C:0.33%, Si:0.52%, Mn:0.80%, P<0.012%, S<0.003%, Cr:0.68%, Mo:0.60%, Ni:0.95%, Ti:0.008-0.030%, Nb:0.015-0.050%, V:0.080-0.150%, B:0.0008-0.0025%, N<0.0040%, 0<0.0025%, and the rest being Fe and unavoidable impurities.
6. The high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB according to claim 1, wherein the steel plates are composed of the following components in weight percentage: C:0.40%, Si:0.51%, Mn:0.64%, P<0.012%, S<0.003%,
Cr:1.00%, Mo:0.42%, Ni:0.80%, Ti:0.008-0.030%, Nb:0.015-0.050%, V:0.080-0.150%, B:0.0008-0.0025%, N50.0040%, 0<0.0025%, and the rest being Fe and unavoidable impurities.
7. The high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB according to claim 1, wherein the steel plates are composed of the following components in weight percentage: C:0.38%, Si:0.60%, Mn:0.30%, P<0.012%, S<0.003%, Cr:0.30%, Mo:0.20%, Ni:0.50%, Ti:0.008-0.030%, Nb:0.015-0.050%, V:0.080-0.150%, B:0.0008-0.0025%, N<0.0040%, 0<0.0025%, and the rest being Fe and unavoidable impurities.
8. A manufacturing method of the high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB as described in any of claims 1-7, comprising the following flow: molten iron desulfurization pretreatment - converter smelting - LF + RH refining - continuous casting or die casting - cast billet hot charging - cast billet heating dephosphorization - rolling - controlled cooling or air cooling - flaw detection - shot blasting quenching - tempering - straightening - cutting - sampling - spray printing of identification inspection - warehousing, wherein the cast billets or steel billets are heated at 1,180-1,220°C and then rolled in the austenite recrystallization region and non-recrystallization region respectively; the rolling requirements in the recrystallization region include pass reduction rate >12%, and finish rolling temperature >980°C; the rolling requirements in the non-recrystallization region include accumulated reduction rate >50%, initial rolling temperature<95 0 °C, and finish rolling temperature >800°C; after rolling, temperature is reduced to room temperature by means of controlled cooling or air cooling, and then off-line heat treatment is performed with the quenching temperature at 820-930°C and the tempering temperature at 100-250°C.
9. The manufacturing method of the high-grade low-alloy wear-resistant steel plates with Brinell hardness of greater than 550HB according to claim 8, wherein the cast billets of continuous casting are 150-300mm thick.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
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| CN201711376683.0 | 2017-12-19 | ||
| CN201711376683.0A CN108018492A (en) | 2017-12-19 | 2017-12-19 | A kind of Brinell hardness is more than the high-level low alloy wear resistance steel plate and manufacture method of 550HB |
| PCT/CN2018/088129 WO2019119725A1 (en) | 2017-12-19 | 2018-05-24 | High-grade low-alloy wear-resistant steel plate having brookfield hardness of greater than 550 hb and manufacturing method |
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| AU2018387506A1 true AU2018387506A1 (en) | 2020-07-30 |
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| CN (1) | CN108018492A (en) |
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| CN108018492A (en) * | 2017-12-19 | 2018-05-11 | 南京钢铁股份有限公司 | A kind of Brinell hardness is more than the high-level low alloy wear resistance steel plate and manufacture method of 550HB |
| CN108754317A (en) * | 2018-06-04 | 2018-11-06 | 南京钢铁股份有限公司 | A kind of low-alloy wear-resistant steel NM400 slabs and manufacturing method |
| CN109055857A (en) * | 2018-08-30 | 2018-12-21 | 武汉钢铁有限公司 | A kind of edge of shovel HB500 grades of martensite wear resistant steels and its processing method |
| CN109811259A (en) * | 2019-01-25 | 2019-05-28 | 南京钢铁股份有限公司 | A kind of ultralow temperature wear-resisting steel plate and manufacturing method |
| CN109811260A (en) * | 2019-01-25 | 2019-05-28 | 南京钢铁股份有限公司 | A kind of extremely cold area wear-resisting steel plate and manufacturing method |
| CN110343952A (en) * | 2019-07-02 | 2019-10-18 | 唐山中厚板材有限公司 | A kind of hardness is not less than the wear-resisting steel plate and its production method of 600HBW |
| CN114184634B (en) * | 2021-12-09 | 2024-02-02 | 贵州师范大学 | Temperature deformation method and device under controllable medium |
| CN115341138B (en) * | 2022-07-12 | 2024-04-19 | 江阴兴澄特种钢铁有限公司 | High-strength protective steel plate and manufacturing method thereof |
| CN115354232B (en) * | 2022-09-06 | 2023-08-11 | 广西科技大学 | Double-phase wear-resistant steel and preparation method thereof |
| CN115382914B (en) * | 2022-09-20 | 2024-06-21 | 钢诺新材料股份有限公司 | Preparation method of superhard wear-resistant forged steel ball |
| CN115637383A (en) * | 2022-10-26 | 2023-01-24 | 东北大学 | 500 HBW-hardness low-alloy high-strength high-hardness martensite protective steel and manufacturing method thereof |
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| JPH0841535A (en) * | 1994-07-29 | 1996-02-13 | Nippon Steel Corp | Production of high hardness wear resistant steel excellent in low temperature toughness |
| CN101497964B (en) * | 2009-03-02 | 2012-06-06 | 暨南大学 | High hardness and toughness low alloy abrasion resistant steel and use thereof |
| DE102011102293A1 (en) * | 2011-02-24 | 2012-08-30 | Stahlwerk Ergste Westig Gmbh | Use of a chromium steel with a martensitic structure and carbide inclusions |
| CN103205634B (en) * | 2013-03-28 | 2016-06-01 | 宝山钢铁股份有限公司 | A kind of low-alloy high hardness wear-resisting steel plate and manufacture method thereof |
| CN106498294A (en) * | 2016-11-08 | 2017-03-15 | 东北大学 | A kind of high-level low-alloy wear-resistant steel of NM600 and its application |
| CN108018492A (en) * | 2017-12-19 | 2018-05-11 | 南京钢铁股份有限公司 | A kind of Brinell hardness is more than the high-level low alloy wear resistance steel plate and manufacture method of 550HB |
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