CN111607741B - Hot-rolled wear-resistant steel with Brinell hardness of more than or equal to 370 and production method thereof - Google Patents
Hot-rolled wear-resistant steel with Brinell hardness of more than or equal to 370 and production method thereof Download PDFInfo
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D11/00—Process control or regulation for heat treatments
- C21D11/005—Process control or regulation for heat treatments for cooling
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- 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
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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
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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 hot-rolled wear-resistant steel with the Brinell hardness of more than or equal to 370 comprises the following components in percentage by weight: c: 0.12 to 0.25%, Si: 0.2-0.9%, Mn: 1.3-1.4%, P is less than or equal to 0.010%, S is less than or equal to 0.004%, Als: 0.02-0.06%, Ti: 0.005-0.03 percent of N, and less than or equal to 0.007 percent of N; the production method comprises the following steps: smelting and casting into a blank by using desulfurized molten iron; heating a casting blank; rough rolling; fine rolling; quickly cooling; coiling; and (5) leveling conventionally. According to the invention, on the premise that the Brinell hardness of the steel plate is not less than 370 and the elongation is not less than 10%, the Brinell hardness of the surface of the steel plate is 371-428 HB, the cold bending property can meet D =5a, the steel plate is qualified at 90 degrees, the impact energy at-20 ℃ is not less than 50J, the production cost can be reduced by at least 20% compared with the prior art, and the unevenness is not more than 4.5 mm/m.
Description
Technical Field
The invention relates to wear-resistant steel and a production method thereof, in particular to hot-rolled wear-resistant steel with Brinell hardness of more than or equal to 370 and a production method thereof, and the hot-rolled wear-resistant steel is particularly suitable for producing wear-resistant steel plates with the thickness of 2-15 mm for mechanical engineering steel.
Background
The wear-resistant steel is one of important basic materials, is widely applied to the fields of mining machinery, coal mining and transportation, engineering machinery, building materials, electric machinery, railway transportation and the like, is in a leading position in research, development and production aspects, and can cover HB 300-600 products of 3-100 mm in thickness specification, such as HARDOX series of Sweden Ochron, XAR series of German theson Krupp and EVERHARD series of Japan JFE.
In recent years, China has obvious progress in the research and development of wear-resistant steel, enterprises can stably supply wear-resistant steel plates with the hardness of HB450 or below in batches, the quality is reliable, and the enterprises are accepted by the market, but the production process is the traditional off-line quenching and tempering process, namely the steel plates need to be subjected to off-line heat treatment, the problems of high alloy cost, long process flow and the like exist, and the relative energy consumption is also high.
The Chinese patent publication No. CN1109919A discloses a low-alloy wear-resistant steel, which comprises the following components in percentage by weight: c: 0.5-0.6%, Si: 0.9-1.2%, Mn: 1.4-1.7%, Cr: 1.35-1.60%, Mo: 0.3-0.5%, V: 0.05-0.10%, Ti: 0.03-0.06%, Re: 0.02-0.04%, although the strength and the wear resistance are good, a large amount of alloy elements for improving hardenability are added, the cost is high, and the content of C, Si is high, so that quenching cracks are easy to generate, and the use of users is influenced.
Chinese patent publication No. CN103114253A discloses "a method for producing ultra-thin ultra-high strength steel sheet", which comprises the following components: 0.12-0.15%, Si: 0-0.1%, Mn: 0.9-1.3%, P is less than or equal to 0.0015%, S is less than or equal to 0.008%, and Ni: 0.35-0.60%, Cr: 0.15-0.30%, Mo: 0.25-0.40%, Ti: 0.008-0.035%, Al: 0.03 to 0.05 percent, the production process comprises the steps of pure steel smelting, hot continuous rolling forming, coil plate flattening, hot rolling substrate quenching and tempering, controlling the heating temperature of a casting blank, exerting the large reduction effect during rolling, excavating the maximum potential energy of heat treatment, ensuring the tissue ultra-fining by a technological means, producing the finished product of the ultra-thin steel plate with the thickness of 3 to 10mm and the ultra-high strength of 1000-plus 1500Mpa, having excellent low-temperature toughness index, having the carbon equivalent of less than or equal to 0.4 percent, having good welding performance and being suitable for large-scale production. However, the waste heat after rolling is not fully utilized, and offline quenching and tempering are required, so that the process route is long, the energy consumption is high, the production cost is high, and the market competitiveness is not strong.
Therefore, the existing wear-resistant steel has the practical problems of high alloy cost, long process flow and the like, so that the component process design is necessary, the process flow is shortened, the production cost is reduced, and the market competitiveness is improved.
Disclosure of Invention
Aiming at the defects of the prior art, the invention provides the hot-rolled wear-resistant steel with the Brinell hardness of more than or equal to 370 and the elongation of more than or equal to 10 percent, which ensures that the Brinell hardness of the steel plate is more than or equal to 370, and the surface of the steel plate has the Brinell hardness of 371-428 HB on the premise of not containing Nb, Mo and B, the cold bending property can meet D =5a, the steel plate is qualified at 90 degrees, the impact energy at-20 ℃ is more than or equal to 50J, and the production cost can be reduced by at least 20 percent, and the hot-rolled wear-resistant steel with the Brinell hardness of more than or equal to 370 and the production method thereof.
The technical measures for realizing the purpose are as follows:
the hot-rolled wear-resistant steel with the Brinell hardness of more than or equal to 370 comprises the following components in percentage by weight: c: 0.12 to 0.25%, Si: 0.2-0.9%, Mn: 1.3-1.4%, P is less than or equal to 0.010%, S is less than or equal to 0.004%, Als: 0.02-0.06%, Ti: 0.005-0.03%, N is less than or equal to 0.007%, the balance is Fe and impurities, and the metallographic structure is lath martensite.
It is characterized in that: the weight percentage content of the added Cr is less than or equal to 0.60 percent.
Preferably: the content of C is 0.12-0.22% by weight.
Preferably: the Ti content is 0.005-0.025 wt%.
Preferably: the weight percentage content of Als is 0.023-0.056%.
Preferably: the weight percentage content of Si is 0.23-0.82%.
The method for producing the hot-rolled wear-resistant steel with the Brinell hardness of more than or equal to 370 comprises the following steps:
1) smelting and casting into a blank by using desulfurized molten iron;
2) heating a casting blank: controlling the ending temperature of the first heating section of the heating furnace to be not lower than 1150 ℃; controlling the ending temperature of the second heating section and the temperature of the soaking section to be 1240-1290 ℃, and controlling the heating time of the second heating section and the soaking time of the soaking section to be not less than 70min in total; controlling the total furnace time to be not less than 150 min; controlling the temperature difference in the plate thickness direction not to exceed 5 ℃;
3) carrying out rough rolling, and controlling the finish temperature of the rough rolling to be 1060-1110 ℃; the thickness of the middle plate is 30-45 mm when the process is finished;
4) performing finish rolling, wherein the initial rolling temperature is controlled to be 950-1050 ℃, the rolling speed is controlled to be 2.0-7.0 m/s, and the finish rolling temperature is controlled to be 820-880 ℃;
5) carrying out quick cooling, cooling to the coiling temperature at the cooling speed of 45-150 ℃/s, controlling the ratio of upper cooling water to lower cooling water to be 45: 55-70: 80, controlling the water pressure to be 1.0-2.5 bar, and adopting a cross side water spraying full-open mode;
6) coiling, wherein the coiling temperature is controlled to be 240-300 ℃; the coiling tension is controlled to be 10-30 tons;
7) and carrying out conventional flattening, and controlling the unevenness not to exceed 4.5 mm/m.
Preferably: the cooling speed is 56-140 ℃/s.
Preferably: the coiling temperature is 240-285 ℃.
The mechanism and action of each component and main process in the invention
C: c is the cheapest element for improving the wear resistance of the material, and the hardness, the strength and the wear resistance are improved along with the increase of the carbon content, but the ductility and the toughness and the welding performance are reduced. Comprehensively, the weight percentage of C is 0.12-0.25%, preferably the weight percentage of C is 0.12-0.22%.
Si: si can obviously reduce the critical cooling speed of the steel, so that the final product forms a refined martensite structure. Among common solid solution elements, Si is only second to P and is dissolved in ferrite and austenite in a solid manner, so that the hardness and the strength can be improved, Si can reduce the diffusion speed of carbon in the ferrite, carbides precipitated during tempering are not easy to aggregate, the tempering stability is improved, the oxidation during friction heating can be reduced, the cold deformation hardening rate and the wear resistance are improved, but quenching cracks are easily generated due to too high Si, and the cracking tendency is larger under ultra-fast cooling. Comprehensively, the weight percentage of Si is 0.2-0.9%, preferably the weight percentage of Si is 0.23-0.82%.
Mn: mn can obviously reduce the Ar1 temperature, the austenite decomposition speed and the martensite transformation temperature of steel, the critical quenching speed of the steel can be obviously reduced by the manganese, the hardness and the strength can be improved by infinite solid solution with Fe, but if the Mn content is too high, the temper brittleness of the steel can be increased, and serious center segregation is caused, and the Mn content is 1.3-1.4% by weight in comprehensive consideration.
And Als: the Als can be deoxidized in the steel and can also play a role in refining grains, and the Als accounts for 0.02-0.06% in comprehensive consideration, and the preferred weight percentage content of the Als is 0.023-0.056%.
Ti: ti and N, O, C both have strong affinity, the affinity with S is stronger than that of iron, the Ti and N, O, C are good deoxidizing and degassing agents and effective elements for fixing N and C, the strength of the steel can be improved, the Ti content by weight is 0.005-0.03% and N, O, C both have strong affinity, the affinity with S is stronger than that of iron, the Ti content by weight is 0.005-0.03% and the Ti content by weight is 0.005-0.025% in comprehensive consideration, and the strength of the steel can be improved.
N: the influence of N on the performance of steel is similar to that of C and P, the strength is obviously improved along with the increase of N content, the plasticity, particularly the toughness is obviously reduced, the weldability is worsened, the cold brittleness is aggravated, the aging tendency is increased, N is easily combined with B in steel to form BN, the effect of B on improving the hardenability is reduced, and the effective B content is reduced, so that the N is less than or equal to 0.007 percent in comprehensive consideration.
P, S: p, S is harmful impurity element in steel, P in steel is easy to form segregation in steel, reduces toughness and welding performance of steel, S is easy to form plastic sulfide, makes steel plate generate layering, and deteriorates steel plate performance, so the lower the P, S content is, the better, comprehensively considering, the P, S content of steel is P less than or equal to 0.010%, and S less than or equal to 0.003%.
According to the invention, the thickness of the intermediate plate is controlled to be 30-45 mm after rough rolling is finished, because the thickness of the intermediate blank is more than 45mm, the reduction rate of the finish rolling stage is increased, on one hand, the increase of the reduction rate enables crystal grains to be refined, the yield ratio of a finished product to be improved, the processability to be reduced, and the difficulty of improving the plate shape of a steel coil in the flattening process after cold is greatly increased, on the other hand, the larger reduction rate enables the rolling load in the finish rolling process to be overlarge, which is not beneficial to producing steel plates with extremely thin specifications and is not beneficial to obtaining excellent rolled plate shape, and when the thickness of the intermediate blank is less than 30mm, the reduction rate of the rough rolling stage is overlarge, the rolling load is large, the limit of equipment is easily exceeded, the normal operation of the equipment is influenced, and the reduction rate of the finish rolling stage is too small, and the mechanical property of the finished product is difficult to guarantee.
The rolling speed is controlled to be 2.0-7.0 m/s in the finish rolling stage, the finish rolling temperature is controlled to be 820-880 ℃, the rolling speed interval is favorable for uniform control of the cooling process, too large or too small rolling speed is not favorable for guaranteeing the quality of the cold plate shape, and the quality of the plate shape is the control key of the method. The final rolling temperature is too high, the cooling strength in the cooling stage is increased, the high cooling strength under the ultra-fast cooling condition deteriorates the cold plate shape quality, and the final rolling temperature is too low, so that the steel plate is easy to enter a two-phase region for rolling, the stability of the rolling process is influenced, ferrite is easy to appear in the finished product structure, and the performance is reduced.
The cooling speed is 45-150 ℃/s, and the ratio of upper cooling water to lower cooling water is controlled to be 45: 55-70: 80, because of too low cooling speed, the cooling uniformity of the steel plate, particularly the steel plate with thick specification in the thickness direction is not easy to ensure, the too high cooling speed ensures that the plate shape quality of the steel plate after cooling is difficult to stabilize under any process, the ratio of the upper cooling water to the lower cooling water can be within the range, the disordered flow of the cooling water on the upper surface is reduced, the cooling uniformity of the upper surface and the lower surface is ensured, and the uniformity of the thickness section is improved.
The coiling temperature is controlled to be 240-300 ℃, and the coiling tension is controlled to be 10-30 tons, because the coiling temperature in the range is favorable for the self tempering of the steel plate to a certain degree, and certain retained austenite can be obtained, the improvement of the processing performance of the steel plate is favorable, the difficulty of improving the plate shape in the flattening process is reduced, the plate shape of the finished steel plate is optimized, and the proper coiling tension can ensure the excellent original coiled shape and the excellent original coiled shape after the tail of the steel plate is subjected to tension loss.
Compared with the prior art, the invention ensures that the Brinell hardness of the steel plate is more than or equal to 370 and the elongation is more than or equal to 10 percent, the Brinell hardness of the surface of the steel plate is 371-428 HB, the cold bending property can meet D =5a, the steel plate is qualified at 90 degrees, the impact energy at minus 20 ℃ is more than or equal to 50J, the production cost can be reduced by at least 20 percent compared with the prior art, and the unevenness is not more than 4.5 mm/m.
Drawings
FIG. 1 is a surface physical diagram of the wear-resistant steel of the present invention;
fig. 2 is a surface physical diagram of the existing wear-resistant steel.
Detailed Description
The present invention is described in detail below:
table 1 is a list of values of chemical components of each example and comparative example of the present invention;
table 2 is a list of values of main process parameters in each example and comparative example of the present invention;
table 3 is a table of the performance tests and results of the examples and comparative examples of the present invention;
each example was produced according to the following procedure:
1) smelting and casting into a blank by using desulfurized molten iron;
2) heating a casting blank: controlling the ending temperature of the first heating section of the heating furnace to be not lower than 1150 ℃; controlling the ending temperature of the second heating section and the temperature of the soaking section to be 1240-1290 ℃, and controlling the heating time of the second heating section and the soaking time of the soaking section to be not less than 70min in total; controlling the total furnace time to be not less than 150 min; controlling the temperature difference in the plate thickness direction not to exceed 5 ℃;
3) carrying out rough rolling, and controlling the finish temperature of the rough rolling to be 1060-1110 ℃; the thickness of the middle plate is 30-45 mm when the process is finished;
4) performing finish rolling, wherein the initial rolling temperature is controlled to be 950-1050 ℃, the rolling speed is controlled to be 2.0-7.0 m/s, and the finish rolling temperature is controlled to be 820-880 ℃;
5) carrying out quick cooling, cooling to the coiling temperature at the cooling speed of 45-150 ℃/s, controlling the ratio of upper cooling water to lower cooling water to be 45: 55-70: 80, controlling the water pressure to be 1.0-2.5 bar, and adopting a cross side water spraying full-open mode;
6) coiling, wherein the coiling temperature is controlled to be 240-300 ℃; the coiling tension is controlled to be 10-30 tons;
7) and carrying out conventional flattening, and controlling the unevenness not to exceed 4.5 mm/m.
TABLE 1 list of chemical compositions (wt%) of inventive and comparative examples
TABLE 2 List of the main process parameters of the examples of the invention and the comparative examples
TABLE 2
TABLE 3 Table of the results of mechanical Properties measurements of the examples of the invention and the comparative examples
As can be seen from Table 3, the Brinell hardness is not less than 370, the elongation is not less than 10%, and on the premise of not containing Nb, Mo and B, the Brinell hardness of the surface of the steel plate is 371-428 HB, the cold bending property can meet D =5a, the steel plate is qualified at 90 degrees, the impact energy at-20 ℃ is not less than 50J, and the production cost can be reduced by at least 20%.
The above examples are merely preferred examples and are not intended to limit the embodiments of the present invention.
Claims (2)
1. The hot-rolled wear-resistant steel with the Brinell hardness of more than or equal to 370 comprises the following components in percentage by weight: c: 0.12 to 0.19%, Si: 0.2 to 0.77%, Mn: 1.3-1.4%, P is less than or equal to 0.010%, S is less than or equal to 0.004%, Als: 0.02-0.06%, Ti: 0.019-0.03%, N is less than or equal to 0.007%, the balance of Fe and impurities, and the metallographic structure is lath martensite;
the production method of the hot-rolled wear-resistant steel with the Brinell hardness of more than or equal to 370 comprises the following steps:
1) smelting and casting into a blank by using desulfurized molten iron;
2) heating a casting blank: controlling the ending temperature of the first heating section of the heating furnace to be not lower than 1150 ℃; controlling the ending temperature of the second heating section and the temperature of the soaking section to be 1240-1290 ℃, and controlling the heating time of the second heating section and the soaking time of the soaking section to be not less than 70min in total; controlling the total furnace time to be not less than 150 min; controlling the temperature difference in the plate thickness direction not to exceed 5 ℃;
3) carrying out rough rolling, and controlling the finish temperature of the rough rolling to be 1060-1110 ℃; the thickness of the middle plate is 30-45 mm when the process is finished;
4) performing finish rolling, wherein the initial rolling temperature is controlled to be 950-1029 ℃, the rolling speed is controlled to be 2.0-4.2 m/s, and the finish rolling temperature is controlled to be 820-845 ℃;
5) carrying out rapid cooling, cooling to the coiling temperature at the cooling speed of 53-150 ℃/s, controlling the ratio of upper cooling water to lower cooling water to be 45: 55-70: 80, controlling the water pressure to be 1.0-2.5 bar, and adopting a cross side water spraying full-open mode;
6) coiling, wherein the coiling temperature is controlled to be 265-300 ℃; the coiling tension is controlled to be 10-30 tons;
7) and carrying out conventional flattening, and controlling the unevenness not to exceed 4.5 mm/m.
2. The hot-rolled wear-resistant steel with Brinell hardness of more than or equal to 370 according to claim 1, wherein: the weight percentage content of the added Cr is less than or equal to 0.60 percent.
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