CN111676418B - Rare earth treated HB500 grade high-wear-resistance steel plate and production method thereof - Google Patents

Rare earth treated HB500 grade high-wear-resistance steel plate and production method thereof Download PDF

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CN111676418B
CN111676418B CN202010380264.XA CN202010380264A CN111676418B CN 111676418 B CN111676418 B CN 111676418B CN 202010380264 A CN202010380264 A CN 202010380264A CN 111676418 B CN111676418 B CN 111676418B
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CN111676418A (en
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袁晓鸣
段承轶
屈文胜
高军
温利军
吴鹏飞
乔建军
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Baotou Iron and Steel Group Co Ltd
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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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21D2211/001—Austenite
    • 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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Abstract

The invention discloses a rare earth treated HB500 grade high-wear-resistance steel plate and a production method thereof. The rare earth treated HB500 grade high-wear-resistance steel plate comprises the following chemical components in percentage by mass: c: 0.25 to 0.30%, Si: 0.15-0.30%, Mn: 1.10-1.40%, P: less than or equal to 0.012%, S: less than or equal to 0.002%, Cr: 0.70-1.00%, Ti: 0.008-0.018%, B: 0.0010-0.0020%, Mo: 0.30 to 0.50%, Ni: 0.30-0.50%, Ce: less than or equal to 0.0015 percent, Als: 0.025 to 0.04%, CEV: 0.60-0.70%, and the balance of iron and inevitable impurities. The steel plate has the characteristics of high strength, high hardness, high low-temperature toughness and high wear resistance.

Description

Rare earth treated HB500 grade high-wear-resistance steel plate and production method thereof
Technical Field
The invention belongs to the field of rare earth high-strength wear-resistant quenched and tempered steel plates, and particularly relates to a rare earth treated HB500 grade high-wear-resistance steel plate and a production method thereof.
Background
Coal is the main energy source in China, and high-performance wear-resistant steel is a key basic material for supporting safe and efficient operation of coal mining and transporting equipment. The working condition environment is extremely complex in the coal mining and transporting process, and the steel plate is subjected to the synergistic effect of multi-factor abrasion (or corrosion) such as coal, gangue, environment media (temperature, humidity and corrosive atmosphere), load stress and the like in the service process. And the region of China is wide, and the working conditions of different mines are greatly different: the content of gangue is about 10% under normal working conditions, and the gangue is normal temperature and humidity; under severe working conditions, the content of gangue can reach 50%, the underground temperature can reach 40 ℃, the humidity is more than 90%, and the abrasion mechanism and the failure behavior of the steel plate under different working conditions are greatly different. The coal mining and transportation typical wear-resistant part, namely the middle groove of the scraper conveyor, has the coal passing amount of about 800 ten thousand tons under the normal working condition, and has the coal passing amount of less than 500 ten thousand tons under the harsh working conditions of high gangue and high humidity and heat. With the increasing high-yield and high-efficiency working faces of millions of tons of annual large mines in China, a novel high-wear-resistance steel plate material is urgently needed to be developed so as to meet the urgent needs of the coal industry.
The low-alloy martensite wear-resistant steel is the wear-resistant steel which is most widely applied in the coal machine industry in China, and compared with the medium-high manganese austenite wear-resistant steel and the bainite wear-resistant steel, the low-alloy martensite wear-resistant steel has the obvious advantages of simple production process, low cost, excellent and stable comprehensive performance and the like, and represents the development direction of the wear-resistant steel for coal mining. However, the conventional low-alloy martensitic steel improves the wear resistance by simply increasing the hardness, which leads to deterioration in the workability of the steel and a significant increase in the tendency of cracking of the wear-resistant member. How to improve the wear resistance without increasing the hardness and reducing the processability is a key technical problem in the development of high-wear-resistance steel for coal mining and transportation.
Document CN102392186A discloses a method for manufacturing HB500 grade low-manganese wear-resistant steel plate, which mainly adopts low-manganese component design, and mainly aims to ensure low-temperature impact toughness and welding performance. The wear-resistant steel plate produced by the components has Brinell hardness of at least HB500 or more, tensile strength of at least 1500MPa, impact toughness of at least 40J/cm at minus 20 ℃ and elongation at break of more than 12 percent, but does not refer to the index of core hardness.
Document CN102943212 discloses an NM500 high-strength wear-resistant steel plate and a heat treatment process thereof, which adopts low-cost component design and a sub-temperature heat treatment process, effectively saves energy and reduces production cost, and the produced NM500 high-strength wear-resistant steel plate has higher strength, good wear resistance, impact toughness and better welding performance, but does not mention the index of core hardness.
Document CN106566993A discloses a NM500 thick plate with excellent low-temperature impact toughness and a production method thereof, which adopts a low-carbon equivalent component design to ensure the welding performance of the steel plate, and adds a proper amount of alloy elements and a proper rolling and heat treatment process, so that the produced steel plate has a uniform and fine structure and excellent comprehensive mechanical properties. The thick plate obtained by the method has the maximum thickness of 80mm, and has the characteristics of moderate strength and excellent low-temperature impact toughness at 1/4-40 ℃ of the plate thickness. But it does not mention the core hardness index.
Disclosure of Invention
In view of one or more of the problems in the prior art, an aspect of the present invention provides a rare earth treated HB500 grade high wear resistance steel sheet, which comprises the following chemical components by mass: c: 0.25 to 0.30%, Si: 0.15-0.30%, Mn: 1.10-1.40%, P: less than or equal to 0.012%, S: less than or equal to 0.002%, Cr: 0.70-1.00%, Ti: 0.008-0.018%, B: 0.0010-0.0020%, Mo: 0.30 to 0.50%, Ni: 0.30-0.50%, Ce: less than or equal to 0.0015 percent, Als: 0.025 to 0.04%, CEV: 0.60-0.70%, and the balance of iron and inevitable impurities.
The mechanical properties of the HB500 grade high-abrasion-resistance steel plate treated by the rare earth meet the following requirements: the yield strength is more than or equal to 1500MPa, the tensile strength is more than or equal to 1580MPa, and the elongation percentage A50The surface Brinell hardness is more than or equal to 20 percent, the surface Brinell hardness is more than or equal to 480HB, the core Brinell hardness is more than or equal to 460HB, the Charpy V-shaped longitudinal impact energy at the temperature of minus 20 ℃ is more than or equal to 40J, and the metallographic structure is a martensite structure and retained austenite.
The thickness of the HB500 grade high-abrasion-resistance steel plate treated by the rare earth is 16-60 mm.
In another aspect, the present invention provides a method for producing the above rare earth treated HB500 grade high wear resistance steel sheet, comprising the steps of:
1) smelting
The molten iron for smelting is subjected to desulfurization pretreatment, scrap steel is added, and the molten steel is subjected to LF refining heating, component fine adjustment and alloying, so that the components and the temperature of the molten steel meet the requirements of subsequent processes; during RH vacuum treatment, the vacuum treatment time is 20min, and rare earth Ce-Fe alloy with required content is added during the vacuum treatment; soft blowing is carried out after RH vacuum treatment is finished;
2) continuous casting
Protective pouring is adopted in the whole continuous casting process, electromagnetic stirring and soft reduction are carried out, and the obtained continuous casting slab is required to have the center segregation not greater than class C3 grade and the center porosity not greater than class 2 grade in low-power detection;
3) rolling of
The temperature of the continuous casting slab out of the furnace is 1200 +/-20 ℃, two-stage rolling is adopted, the initial rolling temperature of rough rolling is more than or equal to 1100 ℃, the finish rolling temperature is 820-870 ℃, and controlled cooling is not needed after rolling to obtain a rolling slab;
4) thermal treatment
Quenching process: heating the rolled plate blank to 860 +/-10 ℃, and keeping the temperature for 30-50 min for quenching to obtain a quenched steel plate;
and (3) tempering process: and (3) heating the quenched steel plate to 200 +/-10 ℃, keeping the temperature for 60-120 min, and then performing air cooling to obtain the rare earth treated HB 500-grade high-wear-resistance steel plate.
The alloy components of the rare earth treated HB500 grade high-wear-resistance steel plate provided based on the technical scheme mainly comprise low carbon and low alloy, the beneficial effects of the rare earth in the aspects of improving the dendrite segregation, the structure morphology, the grain size, the weldability, the formability, the high wear resistance and the like of a casting blank are fully utilized, and the weldability of the wear-resistance steel is improved under the condition that the core hardness of the thick-specification wear-resistance steel is not reduced (example data shows that the core hardness of the obtained steel plate reaches more than 90% of the surface hardness of the steel plate). The mechanical properties of the steel plate meet the requirements that the yield strength is more than or equal to 1500MPa, the tensile strength is more than or equal to 1580MPa, and the elongation percentage A50The surface Brinell hardness is more than or equal to 20 percent, the surface Brinell hardness is more than or equal to 480HB, the core Brinell hardness is more than or equal to 460HB, the Charpy V-shaped longitudinal impact energy at the temperature of minus 20 ℃ is more than or equal to 40J, and the metallographic structure is a martensite structure and residual austenite, so that the high-strength, high-hardness and high-low temperature toughness property are achieved, the service cycle of the product can be obviously prolonged, and the high-strength wear-resistant rare earth is realizedThe wear resistance of the steel is improved by 1.5 times compared with the common wear-resistant steel. According to the production method of the steel plate, the rare earth Ce-Fe alloy is added during RH vacuum treatment, the yield of rare earth can be obviously improved, the stability of performance is ensured, meanwhile, the TMCP process is adopted in the rolling process, and by controlling the process parameters such as the thickness of the intermediate blank, the rolling deformation, the cooling speed and the like, the refining of the casting blank structure and the refining of the hot rolling state structure are realized, the uniformity of the structure is improved, the consistency of hardness in the thickness direction is ensured, and the steel plate with excellent mechanical property, welding property and the like is obtained.
Drawings
FIG. 1 is a metallographic structure photograph of a steel sheet obtained in example 1;
FIG. 2 is a surface scan image of the steel sheet obtained in example 1;
fig. 3 is a schematic structural view of a wear resistance test piece.
Detailed Description
The invention aims to provide a rare earth treated HB500 grade high-wear-resistance steel plate and a production method thereof, wherein rare earth elements are added in the production process, so that the improvement of intergranular embrittlement caused by high chromium content in the steel is facilitated, the austenite stability is improved, the hardenability of the steel plate is improved, the effects of reducing the anisotropy of the steel plate, improving the bending forming performance, reducing the welding cracking tendency, improving the core wear resistance and the like are remarkable, and the weldability of the material is remarkably improved while the core hardness is ensured to reach 90 percent of the surface hardness.
The production method specifically comprises the following steps:
(1) smelting
The molten iron for smelting is subjected to desulfurization pretreatment, high-quality self-produced scrap steel is added, and the molten steel is subjected to LF refining heating, component fine adjustment and alloying, so that the components and the temperature of the molten steel meet the requirements of subsequent processes. And during RH vacuum treatment, the vacuum treatment time is 20min, rare earth Ce-Fe alloy is added during vacuum treatment (experiments prove that the yield of rare earth can reach more than 50 percent by adding the Ce-Fe alloy, which is obviously higher than the yield (less than 30 percent) obtained by directly adding rare earth elements into the system), and the temperature and oxygen are measured before the alloy is added. And soft blowing is carried out after the vacuum treatment is finished, and the slag surface of the steel ladle is kept still during the soft blowing, so that the liquid level of the molten steel cannot be exposed in the air.
(2) Continuous casting
The whole continuous casting process adopts protective casting, and a special anti-oxidation protective casting device made of rare earth steel is used in the casting process. The method ensures that the rare earth steel realizes the goals of no steel flocculation and continuous casting in the casting process. Meanwhile, electromagnetic stirring and soft reduction are carried out, the slab low-power detection requires that the center segregation is not more than class C3, and the center porosity is not more than class 2.
(3) Rolling of
The tapping temperature of the plate blank is 1200 +/-20 ℃. Two-stage rolling is adopted, and the initial rolling temperature of rough rolling is more than or equal to 1100 ℃. And the finish rolling temperature is 820-870 ℃, and cooling control is not needed after rolling.
(4) Heat treatment process
Quenching process: 860 +/-10 ℃, keeping the temperature for 30-50 min, and quenching at the cooling speed of 40 ℃/s;
and (3) tempering process: and keeping the temperature at 200 +/-10 ℃ for 60-120 min for air cooling.
In the following examples, the steel sheets obtained in examples 1 to 3 were collectively referred to as BTNM500 steel sheets.
The present invention will be described in detail below with reference to specific examples, which are provided only for the understanding of the present invention and are not intended to limit the present invention.
Example 1
The chemical composition weight percentage of the steel sheet is shown in table 1 below. The tapping temperature of the heating furnace of the plate blank is 1210 ℃, two-stage rolling is adopted, and the initial rolling temperature of rough rolling is 1150 ℃. The finish rolling temperature is 845 ℃, cooling control is not needed after rolling, and the thickness of the intermediate billet is 3 times that of the finished product. Quenching process: quenching at 867 ℃ for 20min at the cooling speed of 40 ℃/s; and (3) tempering process: keeping the temperature at 204 ℃ for 30min and air cooling. And finally obtaining the steel plate, wherein a metallographic structure photo of the steel plate is shown in figure 1, the metallographic structure of the steel plate is a martensite structure and residual austenite, and the surface scanning component analysis result of the steel plate is shown in figure 2, so that the steel contains rare earth elements.
Example 2
The chemical composition weight percentage of the steel sheet is shown in table 1 below. The tapping temperature of the heating furnace of the plate blank is 1205 ℃, and the plate blank is rolled in time after being heated. Two-stage rolling is adopted, and the initial rolling temperature of rough rolling is more than or equal to 1160 ℃. The finish rolling temperature of the finish rolling is 835 ℃, the thin specification does not need to be controlled to be cold, and the thickness of the intermediate billet is 3 times that of the finished product. Quenching process: quenching at 862 deg.C for 30 min; and (3) tempering process: keeping the temperature at 210 ℃ for 50min and cooling in air. And finally obtaining the steel plate.
Example 3
The chemical composition weight percentage of the steel sheet is shown in table 1 below. The tapping temperature of the heating furnace of the plate blank is 1205 ℃, and the plate blank is rolled in time after being heated. Two-stage rolling is adopted, and the initial rolling temperature of rough rolling is more than or equal to 1160 ℃. The finish rolling temperature is 840 ℃, the controlled cooling is not needed for thin specifications, and the thickness of the intermediate billet is 3 times that of a finished product. Quenching process: quenching at 854 deg.c for 40 min; and (3) tempering process: keeping the temperature at 204 ℃ for 70min and cooling in air. And finally obtaining the steel plate.
Comparative example 1
The chemical composition weight percentage of the steel sheet is shown in table 1 below. The tapping temperature of the heating furnace of the plate blank is 1205 ℃, and the plate blank is rolled in time after being heated. Two-stage rolling is adopted, and the initial rolling temperature of rough rolling is more than or equal to 1160 ℃. The finish rolling temperature is 831 ℃, the thin specification does not need controlled cooling, and the thickness of the intermediate billet is 3 times of that of the finished product. Quenching process: quenching at 870 ℃ for 20 min; and (3) tempering process: keeping the temperature at 207 ℃ for 120min and cooling in air. And finally obtaining the steel plate.
Table 1: chemical composition of steel plate (wt%)
Figure BDA0002481710010000041
Figure BDA0002481710010000051
Detection experiment 1
Mechanical property tests were performed on the wear-resistant steel sheets obtained in examples 1 to 3 and comparative example 1, and the results are shown in table 2 below.
Table 2: mechanical properties of steel plate
Figure BDA0002481710010000052
As can be seen from Table 2 above, the steel sheets of examples 1 to 3 had tensile strengths: 1588-1665 MPa, elongation: 20.5% -27.0%, surface brinell hardness: 487-499 HB, Brinell hardness of the core: 458-472 HB, Charpy V-shaped longitudinal impact energy at-20 ℃: 42-48J, it can be seen that the steel sheet has a core hardness of 90% or more of the surface hardness (the surface hardness and the core hardness do not directly correspond to each other, the quenched steel sheet generally has a hardened layer of a certain thickness, the thickness of the hardened layer is related to the amount of hardenability elements, if the hardenability elements are small, the surface is hard, and the hardened layer is thin, and is not quenched through to the core, and thus the core hardness is low, and therefore, the core hardness cannot be directly calculated from the surface hardness), whereas the steel sheet obtained in comparative example 1 is inferior to the steel sheets of examples 1-3 in terms of the steel sheet strength and charpy V-type longitudinal impact power at-20 ℃, and the steel sheet obtained in comparative example 1 has a core hardness of only 77% of the surface hardness, which is significantly lower than the core hardness of the steel sheets of examples 1-3, and therefore, the wear resistance is inferior to the steel sheets of examples 1-3. The data show that the wear-resistant steel plate provided by the invention not only has the characteristics of high strength, high hardness, high elongation and the like, but also has excellent cold-bending forming performance, and the strength, hardness, elongation, impact and bending of the steel plate are obviously superior to those of the steel plate in the comparative example 1.
Detection experiment 2
This test was conducted by testing the wear resistance of the steel sheet of example 1 (three replicates corresponding to sample numbers N1, N2, N3) and comparing it with the wear resistance of HADOX500 steel sheet (three replicates corresponding to sample numbers H1, H2, H3) produced by SSAB corporation, sweden.
The abrasion resistance test was carried out on an MLS-225 type wet rubber wheel abrasive abrasion tester, and an abrasive abrasion test was carried out by cutting and processing a sample piece having a size of 57.0mm by 25.5mm by 7.0mm from the surface in the thickness direction with a wire cutting apparatus, the sample piece being as shown in FIG. 3. The test is completed on a wet-type rubber wheel abrasive wear testing machine, and the friction medium is water and silt. The results of the measurements are shown in Table 3 below.
Table 3: wear results of BTNM500 and comparative materials
Figure BDA0002481710010000061
As can be seen from the data in table 3, the average wear amount of the BTNM500 of the steel plate obtained in example 1 is 0.1386g, which is significantly lower than the wear amount 0.20576g of the existing NM500 steel plate, and the test results show that the rare earth high strength wear resistant steel BTNM500 provided by the present invention has excellent wear resistance.
Finally, it should be noted that: although the present invention has been described in detail with reference to the foregoing embodiments, it will be apparent to those skilled in the art that changes may be made in the embodiments and/or equivalents thereof without departing from the spirit and scope of the invention. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.

Claims (2)

1. The rare earth treated HB500 grade high-wear-resistance steel plate is characterized by comprising the following chemical components in percentage by mass: c: 0.25 to 0.30%, Si: 0.15-0.30%, Mn: 1.10-1.40%, P: less than or equal to 0.012%, S: less than or equal to 0.002%, Cr: 0.70-1.00%, Ti: 0.008-0.018%, B: 0.0010-0.0020%, Mo: 0.30 to 0.50%, Ni: 0.30-0.50%, 0.0014% to 0.0015% of Ce, Als: 0.025 to 0.04%, CEV: 0.60-0.70%, and the balance of iron and inevitable impurities;
the core Brinell hardness of the HB500 grade high-wear-resistance steel plate treated by the rare earth is more than 90 percent of the surface Brinell hardness;
the production method of the rare earth treated HB500 grade high-wear-resistance steel plate comprises the following steps:
1) smelting
The molten iron for smelting is subjected to desulfurization pretreatment, scrap steel is added, and the molten steel is subjected to LF refining heating, component fine adjustment and alloying, so that the components and the temperature of the molten steel meet the requirements of subsequent processes; during RH vacuum treatment, the vacuum treatment time is 20min, and rare earth Ce-Fe alloy with required content is added during the vacuum treatment; soft blowing is carried out after RH vacuum treatment is finished;
2) continuous casting
Protective pouring is adopted in the whole continuous casting process, electromagnetic stirring and soft reduction are carried out, and the obtained continuous casting slab is required to have the center segregation not greater than class C3 grade and the center porosity not greater than class 2 grade in low-power detection;
3) rolling of
The temperature of the continuous casting slab out of the furnace is 1200 +/-20 ℃, two-stage rolling is adopted, the initial rolling temperature of rough rolling is more than or equal to 1100 ℃, the finish rolling temperature is 820-870 ℃, and uncontrolled cooling is carried out after rolling to obtain a rolling slab;
4) thermal treatment
Quenching process: heating the rolled plate blank to 860 +/-10 ℃, keeping the temperature for 30-50 min, quenching, and cooling to room temperature at a cooling speed of 40 ℃/s to obtain a quenched steel plate;
and (3) tempering process: heating the quenched steel plate to 200 +/-10 ℃, keeping the temperature for 60-120 min, and then air-cooling to obtain a rare earth treated HB500 grade high-wear-resistance steel plate;
the mechanical properties of the rare earth treated HB500 grade high-abrasion-resistance steel plate meet the following requirements: the yield strength is more than or equal to 1500MPa, the tensile strength is more than or equal to 1580MPa, and the elongation percentage A50The surface Brinell hardness is more than or equal to 20 percent, the surface Brinell hardness is more than or equal to 480HB, the core Brinell hardness is more than or equal to 460HB, the Charpy V-shaped longitudinal impact energy at the temperature of minus 20 ℃ is more than or equal to 40J, and the metallographic structure is a martensite structure and retained austenite.
2. The rare earth-treated HB500 grade high wear resistance steel sheet according to claim 1, wherein the thickness of the rare earth-treated HB500 grade high wear resistance steel sheet is 16-60 mm.
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