CN113215490A - Thin HB 300-grade wear-resistant steel plate and manufacturing method thereof - Google Patents
Thin HB 300-grade wear-resistant steel plate and manufacturing method thereof Download PDFInfo
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
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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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- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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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
- C21D2211/005—Ferrite
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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
Abstract
The invention provides a thin HB 300-grade wear-resistant steel plate and a manufacturing method thereof, wherein the thin HB 300-grade wear-resistant steel plate comprises the following components: 0.12 to 0.22 percent; si: 0.80-1.40%; mn: 1.0-2.0%; p: less than or equal to 0.020%; s: less than or equal to 0.010 percent; ti: 0.010-0.060%; cr: 0.10 to 0.40 percent; 0 to 0.20 percent of Mo; b: 0.0008-0.0020%; and Als: 0.020-0.060%; the balance of Fe and inevitable impurities; compared with the prior art, the invention can obviously shorten the production process flow and reduce the production cost while ensuring the strength, hardness and wear resistance of the material and improving the cold-bending forming performance; the method can be used for manufacturing high-strength structural members of engineering machinery such as concrete mixing tank bodies, dump truck compartments and the like.
Description
Technical Field
The invention belongs to the technical field of wear-resistant steel production processes, and particularly relates to a thin HB 300-grade wear-resistant steel plate and a manufacturing method thereof.
Background
With the comprehensive implementation of policies such as overload control, energy conservation and environmental protection, the development of light weight, heavy load and long service life of the special vehicle industry has become a necessary trend. The high-strength steel is one of the most direct and effective ways for light weight, and the trend of thin standardization and high reinforcement of the special automotive steel is more and more obvious. The wear-resistant steel has high strength, high hardness and high wear resistance, and is widely applied to manufacturing wear-resistant structural parts of various special vehicle types and the like.
At present, the most widely applied traditional low-alloy wear-resistant steel is usually added with noble alloy elements such as Cr, Mo, Ni and rare earth in the design of chemical components, and the strong hardness and the low-temperature impact toughness of the material are improved by utilizing fine-grain strengthening, solid solution strengthening, precipitation strengthening and the like; the main production technology mainly comprises two processes of hot rolling, quenching and tempering heat treatment and hot rolling and tempering heat treatment, the improvement of the material strength and the wear resistance mainly depends on the heat treatment process, and no precedent for realizing the HB 300-grade wear-resistant steel plate by the hot rolling TMCP process exists; the microstructure is tempered martensite or tempered martensite plus retained austenite, and the aim of improving the wear resistance of the material is achieved mainly by regulating and controlling the microstructure characteristics of the martensite and improving the hardness of the martensite.
Therefore, on one hand, the traditional low-alloy wear-resistant steel has complex chemical component design, long process flow, long production period, high energy consumption and high production cost; on the other hand, the product structure after heat treatment is tempered martensite or tempered martensite and retained austenite, the structure internal stress is large, the yield ratio is high, the cold-bending forming performance is limited, and only 90 degrees can be ensured, and D is 6a (D-bending pressure head diameter, a-sample thickness) is qualified.
Disclosure of Invention
The invention aims to provide a thin HB 300-grade wear-resistant steel plate, the tensile strength of which is more than or equal to 1050MPa, and the elongation percentage A of which is50Not less than 15 percent and low-temperature impact property A at-20 DEG CkvThe product has the advantages of more than or equal to 20J (sample size: 2.5 multiplied by 10 multiplied by 55mm), the surface Brinell hardness of more than or equal to 300HB, the cold bending property of 180 degrees, and qualified D-2 a, and the product performance meets the technical requirement of HB300 level in GB/T24186-2009, so that the production process flow can be shortened and the production cost can be obviously reduced while the strength, the hardness and the wear resistance of the material are ensured and the cold bending forming property is improved.
The invention also aims to provide a manufacturing method of the thin HB 300-grade wear-resistant steel plate, which adopts a heat treatment-free process and combines with an alloy component optimization and matched TMCP process, so that the production process flow is obviously shortened and the production cost is reduced while the strength, the hardness and the wear resistance of the material are ensured and the cold bending forming performance is improved. The wear-resistant steel can be used for manufacturing high-strength structural members of engineering machinery such as concrete mixing tank bodies, dump truck compartments and the like.
The specific technical scheme of the invention is as follows:
a thin specification HB300 level wear-resistant steel plate comprises the following chemical components in percentage by weight: c: 0.12 to 0.22 percent; si: 0.80-1.40%; mn: 1.0-2.0%; p: less than or equal to 0.020%; s: less than or equal to 0.010 percent; ti: 0.010-0.060%; cr: 0.10 to 0.40 percent; 0 to 0.20 percent of Mo; b: 0.0008-0.0020%; and Als: 0.020-0.060%; the balance of Fe and inevitable impurities.
The carbon equivalent CEV of the thin HB 300-grade wear-resistant steel plate is less than or equal to 0.55 percent, and good welding performance is achieved.
The thin specification HB300 grade wear-resistant steel plate has a microstructure of martensite and ferrite, wherein the volume fraction of the martensite is 60-70%, the equivalent grain size of the martensite is 10-20 μm, the volume fraction of the ferrite is 30-40%, and the average grain size of the ferrite is 4-10 μm;
the thickness of the thin HB 300-grade wear-resistant steel plate is 3-6 mm;
the thin HB 300-grade wear-resistant steel plate has the tensile strength of more than or equal to 1050MPa and the elongation percentage A50The abrasion-resistant steel has the advantages that the abrasion-resistant steel is larger than or equal to 15 percent, the low-temperature impact performance Akv at the temperature of-20 ℃ is larger than or equal to 20J (the sample size is 2.5 multiplied by 10 multiplied by 55mm), the surface Brinell hardness is larger than or equal to 300HB, the cold bending performance is 180 degrees, D is qualified as 2a, and the product performance meets the technical requirements of HB 300-grade abrasion-resistant steel in GB/T24186-2009.
The manufacturing method of the thin HB 300-grade wear-resistant steel plate comprises rolling;
the rolling adopts a two-stage controlled rolling process, the rough rolling accumulated reduction rate is more than or equal to 80 percent, and the finish rolling accumulated reduction rate is more than or equal to 80 percent;
further, the initial rolling temperature of rough rolling is 1100-.
The manufacturing method further includes heating, the heating being performed before rolling;
the heating is as follows: and (3) heating the casting blank in a heating furnace at 1150-1200 ℃ for 2-2.5 h.
Further, the manufacturing method further comprises smelting and forging, and the smelting and forging are carried out before heating.
The smelting refers to smelting in a vacuum furnace.
The forging refers to forging the smelted casting blank into a rectangular blank.
Further, the manufacturing method further includes cooling, the cooling being performed after the rolling.
And the cooling adopts a three-section laminar flow cooling mode, the steel plate after finish rolling is cooled for 1-2s at a cooling speed of more than 80 ℃/s and then is subjected to air cooling, the steel plate is cooled to 650-350 ℃ after air cooling for 5-8s, then the steel plate is cooled at a cooling speed of more than or equal to 50 ℃/s, the final cooling temperature is controlled to be 250-350 ℃, and finally the steel plate is subjected to air cooling to room temperature.
The main elements in the chemical components of the invention and the functions thereof are as follows:
c: 0.12-0.22%, C is used as a basic element in the steel and plays a very important role in improving the tensile strength, hardness and wear resistance of the steel, the volume fraction and the hardness of martensite are directly influenced by the content of C, the volume fraction and the hardness of the martensite cannot be ensured when the content of C is too low, and further the strength and the wear resistance of the material cannot be ensured, in order to obtain higher tensile strength, hardness and wear resistance, the content of C is not less than 0.12%, but the content of C is too high, a certain amount of soft-phase ferrite tissues are difficult to form after rolling and cooling, the proportion of hard-phase martensite is higher, and further the ductility and toughness of the material can be influenced;
si: 0.80-1.40%, adding a proper amount of Si, not only playing a role of solid solution strengthening, increasing the strength and hardness of steel, but also promoting the formation of soft-phase ferrite in a laminar cooling air-cooling section and expanding a cooling process window formed by the soft-phase ferrite in the air-cooling section, wherein the effect of Si is shown when the content of Si reaches more than 0.80%, but the content of Si is not too high, and the content of Si is too high, so that on one hand, a large amount of red iron scales are generated on the surface of a material to influence the surface quality of the product, based on the control of the surface iron scales, the heating temperature is not more than 1200 ℃, and meanwhile, low-temperature rolling is adopted, and the final rolling temperature is not more than 850 ℃; on the other hand, the proportion of the generated soft phase ferrite is too high, so that the strength and the hardness of the product are reduced;
mn: 1.0-2.0%, Mn is used as a reinforcing element of the steel, the hardenability of the steel can be obviously improved, the strength of the steel is improved, in order to ensure the strength of the steel, the Mn content is controlled to be more than 1.0%, but the Mn content cannot be too high, and the Mn content is too high, a part of C content corresponding to the invention belongs to the category of peritectic steel (C is 0.08-0.16%), on one hand, the possibility of casting blank segregation and longitudinal cracking is increased, on the other hand, Mn delays the pearlite transformation and also delays the ferrite transformation, so that a certain amount of ferrite is not easily formed after cooling after rolling, and the forming performance of the steel is adversely affected.
P, S as impurity elements, which increase the brittleness of steel and adversely affect the plasticity, toughness and the like of steel, should be strictly controlled, the lower the content, the better, the cost factor is considered, and the P: less than or equal to 0.020%, S: less than or equal to 0.010 percent;
cr: 0.10-0.40%, Cr is used as medium-strength carbide forming element, the affinity with carbon is strong, and the comprehensive action of Mn makes pearlite transformation obviously delayed and the hardenability of steel is obviously improved. Meanwhile, Cr is an element for stabilizing austenite, so that the transformation of pearlite and ferrite is delayed strongly, and the transformation of bainite can be inhibited strongly when Cr and Mn are mixed after final cooling, so that the cooling process window is enlarged, but the content of Cr is too high, so that formed carbides (Cr23C6 and Cr7C3) are coarse, and the formability of steel is not favorable. Therefore, 0.10 to 0.40% of Cr needs to be added in view of avoiding pearlite and bainite transformation during cooling and improving strength and hardness of the material.
Mo: 0-0.20%, Mo can delay pearlite transformation and improve laminar cooling process window. Meanwhile, the biggest advantage of Mo is that the alloy has good high-temperature thermal stability, the size of TiC second-phase precipitate particles formed in an air cooling section can be controlled, and the TiC particles are prevented from being coarsened seriously.
Ti: 0.010-0.060%, Ti plays two main roles in steel, firstly, a hard TiC second phase precipitate can be formed in a laminar cooling air cooling section, the precipitation strengthening effect can be achieved, and the material strength and the wear resistance are obviously improved; and secondly, the welding performance of the material is improved, and TiN formed by combining Ti and N has an obvious inhibiting effect on austenite grain coarsening in the welding process.
B: 0.0008 to 0.0020%, B is added mainly to increase the hardenability of the steel, the hardenability is remarkably improved when the B content reaches 0.0008%, but when the B content is not too high and the B content is more than 0.0020%, B is used as a stable austenite region element, the transformation of austenite to ferrite is strongly delayed, a certain proportion of ferrite is difficult to form even by prolonging the air cooling time, or the supercooling degree is increased by reducing the air cooling section temperature, the driving force of the transformation of austenite to ferrite is increased, bainite transformation occurs, and the cooling process window is narrowed, so the B content is preferably controlled to 0.0010 to 0.0020%.
And Als: 0.020-0.060 percent of Als, which is mainly used as a deoxidizer and can react with N to generate AlN spiked grain boundaries to play a role in grain refinement, and if the content of Als is too high, the generated coarse AlN particles have a reduced grain refinement effect on the material.
In the design of a hot rolling process, the material strengthening is mainly phase transformation strengthening, fine grain strengthening and precipitation strengthening, the target microstructure is martensite and ferrite, the martensite is mainly, hard phase martensite is used for improving the strength, hardness and wear resistance of the material, and soft phase ferrite is used for improving the plasticity and toughness and cold bending forming performance of the material. The heating temperature is controlled to 1150-1200 ℃, and the main purpose is to prevent the influence on the surface quality of the strip steel caused by the fact that the heating temperature is too high and the scale is thick and difficult to remove; the finishing temperature is controlled at 800-850 ℃, the lower finishing temperature is favorable for fully refining the original austenite grain size and improving the fine grain strengthening effect, and meanwhile, the thickness of the iron scale can be reduced by low-temperature rolling considering that the chemical element contains a higher content of Si element. After rolling, a three-stage cooling process is adopted: the first section cooling speed is controlled to be more than 80 ℃/s, the purpose is to enable the material to rapidly enter a ferrite phase change area, and refine ferrite grains, thereby being beneficial to improving the cold-bending forming performance and the impact performance of the material; the second stage air cooling time is controlled to be 5-8s, the second stage final cooling temperature is controlled to be 650-700 ℃, the purpose is to obtain a ferrite structure with a certain proportion, and the air cooling time is too long, the proportion of ferrite is more, and the size of ferrite grains is large, but the improvement of the strength and the hardness of the material is not facilitated; the air cooling finishing temperature is more than 700 ℃, the supercooling degree is low, and the phase change driving force is low, so that the ferrite structure proportion is small, the ferrite grain size growth speed is high, and the ferrite grain size is large; the air cooling finishing temperature is too low, particularly lower than 600 ℃, although a certain proportion of ferrite can be obtained, a certain proportion of bainite tissues can be generated at the same time, and the high tensile strength and high hardness are not easily obtained; the cooling speed of the third section is controlled to be more than 50 ℃/s, the final cooling temperature of the third section is controlled to be 250-350 ℃, the purpose is to enable the untransformed austenite structure to be rapidly transformed into a martensite structure, so that the material finally obtains a martensite + ferrite structure, the final cooling temperature is too high, the transformed martensite is self-tempered, and the decomposition in the martensite can reduce the strength of the material; the final cooling temperature is too low, the temperature fluctuation in the width direction of the plate is large, and the temperature uniformity, the stability of the mechanical properties of the material and the shape of the plate are difficult to ensure.
The invention produces the wear-resistant steel with the corresponding grade according to the service environment and the economical efficiency of the material, and improves the cold-bending forming performance of the material while ensuring the wear resistance of the material. The hot rolled steel plate provided by the invention has a microstructure of martensite and ferrite, wherein the volume fraction of the martensite is 60-70%, the equivalent grain size of the martensite is 10-20 mu m, the volume fraction of the ferrite is 30-40%, and the average grain size of the ferrite is 4-10 mu m. Tensile strength is more than or equal to 1050MPa, and elongation percentage A50The abrasion-resistant steel has the advantages that the abrasion-resistant steel is larger than or equal to 15 percent, the low-temperature impact performance Akv at the temperature of-20 ℃ is larger than or equal to 20J (the sample size is 2.5 multiplied by 10 multiplied by 55mm), the surface Brinell hardness is larger than or equal to 300HB, the cold bending performance is 180 degrees, D is qualified as 2a, and the product performance meets the technical requirements of HB 300-grade abrasion-resistant steel in GB/T24186-2009.
Drawings
FIG. 1 a metallographic structure diagram of a hot rolled steel sheet produced in example 1;
FIG. 2 metallographic structure drawing of a hot rolled steel sheet produced in example 2;
FIG. 3 metallographic structure drawing of a hot rolled steel sheet produced in example 3;
FIG. 4 metallographic structure drawing of a hot rolled steel sheet produced in example 4;
FIG. 5 is a metallographic structure chart of a hot rolled steel sheet produced in comparative example 1;
FIG. 6 is a metallographic structure chart of a hot rolled steel sheet produced in comparative example 2.
Detailed Description
The technical scheme of the present invention will be described below by way of specific examples and comparative examples.
A thin specification HB300 level wear-resistant steel plate comprises the following chemical components in percentage by weight: c: 0.12 to 0.22 percent; si: 0.80-1.40%; mn: 1.0-2.0%; p: less than or equal to 0.020%; s: less than or equal to 0.010 percent; ti: 0.010-0.060%; cr: 0.10 to 0.40 percent; 0 to 0.20 percent of Mo; b: 0.0008-0.0020%; and Als: 0.020-0.060%; the balance of Fe and inevitable impurities.
The thin HB 300-grade wear-resistant steel plate has a microstructure of martensite and ferrite, wherein the volume fraction of the martensite is 60-70%, the equivalent grain size of the martensite is 10-20 mu m, the volume fraction of the ferrite is 30-40%, and the average grain size of the ferrite is 4-10 mu m.
Examples 1 to 5, comparative examples 1 to 2
A thin HB300 grade wear-resistant steel plate has the chemical composition shown in Table 1, and the balance not shown in Table 1 is Fe and inevitable impurities.
TABLE 1 actual measured chemical composition (mass percent, wt%) of each example and comparative example
| Numbering | C | Si | Mn | P | S | Cr | Mo | Ti | B | Als | CEV |
| Example 1 | 0.13 | 1.15 | 1.86 | 0.011 | 0.006 | 0.36 | 0 | 0.028 | 0.0012 | 0.040 | 0.51 |
| Example 2 | 0.14 | 1.04 | 1.80 | 0.009 | 0.005 | 0.30 | 0.08 | 0.024 | 0.0015 | 0.035 | 0.52 |
| Example 3 | 0.15 | 1.13 | 1.75 | 0.008 | 0.007 | 0.27 | 0.10 | 0.020 | 0.0013 | 0.033 | 0.52 |
| Example 4 | 0.19 | 0.95 | 1.20 | 0.008 | 0.003 | 0.21 | 0.15 | 0.025 | 0.0018 | 0.038 | 0.46 |
| Example 5 | 0.15 | 0.90 | 1.65 | 0.008 | 0.003 | 0.30 | 0.20 | 0.055 | 0.0018 | 0.055 | 0.53 |
| Comparative example 1 | 0.16 | 1.10 | 1.78 | 0.008 | 0.005 | 0.25 | 0.15 | 0.036 | 0.0011 | 0.033 | 0.54 |
| Comparative example 2 | 0.10 | 1.01 | 1.30 | 0.009 | 0.004 | 0.15 | 0.10 | 0.025 | 0.0010 | 0.045 | 0.37 |
Carbon equivalent CEV ═ C + Mn/6+ (Cr + Mo + V)/5+ (Ni + Cu)/15] × 100%.
The production method of the thin HB 300-grade wear-resistant steel plate comprises the following processes of smelting, forging, heating, hot rolling and cooling:
1) smelting and forging, smelting in a vacuum furnace according to the chemical components in the table 1, and forging the smelted casting blank into a rectangular blank;
2) heating, wherein the casting blank enters a heating furnace for heating, the heating temperature is 1150-1200 ℃, and the heat preservation time is 2-2.5 h;
3) rolling, namely, controlling a rolling process in two stages, wherein the rough rolling accumulated reduction rate is more than or equal to 80 percent, and the finish rolling accumulated reduction rate is more than or equal to 80 percent; the initial rolling temperature of rough rolling is 1100-1150 ℃, and the final rolling temperature of finish rolling is 800-850 ℃.
4) And (3) cooling: and (3) adopting a three-section cooling mode, cooling the finish-rolled steel plate for 1-2s at a cooling speed of more than 80 ℃/s, then carrying out air cooling, cooling for 5-8s to 650-350 ℃, cooling the steel plate at a cooling speed of more than or equal to 50 ℃/s, controlling the final cooling temperature to 250-350 ℃, and finally carrying out air cooling to room temperature.
Specific rolling process parameters of examples 1 to 5 and comparative examples 1 to 2 are shown in table 2, the microstructure composition phase proportion and size are shown in table 3, the mechanical properties of examples 1 to 5, comparative examples 1 to 2 and conventional heat-treated wear-resistant steels NM300, comparative examples 3 to 4 are shown in table 4, and the abrasion weight loss data are shown in table 5. It can be seen that the strength, elongation and hardness of the steel plate in the embodiment of the invention all reach the level of the traditional NM300 material object, and the steel plate has better cold bending performance, lower wear weight loss and better wear resistance.
TABLE 2 Main Rolling Process parameters of examples and comparative examples
TABLE 3 proportion and size of phase composition of microstructure of each of examples and comparative examples
TABLE 4 mechanical properties of the examples and comparative examples
Note: comparative examples 3 and 4 are conventional NM300 steel sheets produced by quenching and tempering heat treatment, and the production processes of chemical composition, rolling and heat treatment are as follows:
comparative example 3:
the traditional NM300 steel plate comprises the following components: c: 0.13 percent; si: 0.35 percent; mn: 1.35 percent; p: 0.012%; s: 0.003%; mo: 0.25 percent; v: 0.035%; b: 0.0015 percent; ti: 0.025 percent; and Als: 0.029%. The manufacturing process comprises the following steps: the molten steel is smelted in a converter or an electric furnace and refined outside the furnace, and is cast into a plate blank. The heating temperature of the plate blank is 1200 ℃, the initial rolling temperature is 1150 ℃, the final rolling temperature is 910 ℃, and the plate blank is air-cooled to the room temperature after being rolled. The steel plate heat treatment process comprises quenching and tempering, wherein the quenching temperature is 910 ℃, and the heat preservation time is 20 mmin; the tempering process comprises the following steps: tempering temperature is 260 ℃, heat preservation is carried out for 60min, and the thickness specification of the finished product is 5 mm.
Comparative example 4:
the traditional NM300 steel plate comprises the following components: c: 0.14 percent; si: 0.30 percent; mn: 1.29 percent; p: 0.010%; s: 0.003%; mo: 0.30 percent; v: 0.030%; b: 0.0018%; ti: 0.020%; and Als: 0.036%. The manufacturing process comprises the following steps: the molten steel is smelted in a converter or an electric furnace and refined outside the furnace, and is cast into a plate blank. The heating temperature of the plate blank is 1190 ℃, the initial rolling temperature is 1145 ℃, the final rolling temperature is 900 ℃, and the plate blank is air-cooled to the room temperature after being rolled. The steel plate heat treatment process comprises quenching and tempering, wherein the quenching temperature is 910 ℃, and the heat preservation time is 20 mmin; the tempering process comprises the following steps: tempering temperature is 250 ℃, and heat preservation is carried out for 50min, and the thickness specification of the finished product is 4 mm.
Table 5 abrasion loss data for abrasion resistance tests of examples and comparative examples
| Numbering | Loss on abrasion Δ m (g) |
| Example 1 | 1.8812 |
| Example 2 | 1.8691 |
| Example 3 | 1.8613 |
| Example 4 | 1.8132 |
| Example 5 | 1.8016 |
| Comparative example 1 | 2.1614 |
| Comparative example 2 | 2.1452 |
| COMPARATIVE EXAMPLE 3(NM300) | 1.9598 |
| COMPARATIVE EXAMPLE 4(NM300) | 1.9554 |
Note: the abrasive wear test was performed in an MLS-225 type wet rubber wheel testing machine, and the sample size of the abrasive wear test was: 57mm (length) × 25.5mm (width) × 2.5mm (thickness), wherein the 57mm × 25.5mm face is the wear face, the wear surface is polished. The test parameters were as follows: the hardness of the rubber wheel is 60HS, the rotating speed of the rubber wheel is 240r/min, the grinding material is a solution formed by mixing quartz sand and water according to the proportion of 1:1, the particle size of the quartz sand is 20-40 meshes, and the load is 170N. Firstly, pre-grinding the wear surface of a sample by 1000r, recording the weight m1 of the pre-ground sample, then carrying out accurate grinding for 40min, recording the weight m2 of the accurately ground sample, carrying out ultrasonic cleaning on the pre-ground sample and the accurately ground sample, and measuring the weight by an electronic balance (the precision is 0.1 mg). The abrasion weight loss delta m (m1-m2) is used as a main parameter for evaluating the abrasion resistance of the material, and the smaller the abrasion weight loss is, the better the abrasion resistance of the material is. And (3) respectively selecting 3 pieces of each test material under the same test condition to carry out an abrasive wear test, and taking the average value of the wear weight loss of the 3 samples as the final wear weight loss.
The invention produces the wear-resistant steel with the corresponding grade according to the service environment and the economical efficiency of the material, and improves the cold-bending forming performance of the material while ensuring the wear resistance of the material. The method can be used for manufacturing high-strength structural members of engineering machinery such as concrete mixing tank bodies, dump truck compartments and the like.
Claims (10)
1. The thin specification HB 300-grade wear-resistant steel plate is characterized by comprising the following chemical components in percentage by weight: 0.12 to 0.22 percent; si: 0.80-1.40%; mn: 1.0-2.0%; p: less than or equal to 0.020%; s: less than or equal to 0.010 percent; ti: 0.010-0.060%; cr: 0.10 to 0.40 percent; 0 to 0.20 percent of Mo; b: 0.0008-0.0020%; and Als: 0.020-0.060%; the balance of Fe and inevitable impurities.
2. The thin gauge HB300 grade wear resistant steel plate of claim 1, wherein said thin gauge HB300 grade wear resistant steel plate has a carbon equivalent CEV ≦ 0.55%.
3. The thin gauge HB300 grade wear resistant steel plate of claim wherein the thin gauge HB300 grade wear resistant steel plate microstructure is martensite + ferrite with a martensite volume fraction of 60-70%, a martensite equivalent grain size of 10-20 μm, a ferrite volume fraction of 30-40%, and a ferrite average grain size of 4-10 μm.
4. The thin gauge HB300 grade wear resistant steel plate of claim 1 or 32 wherein said thin gauge HB300 grade wear resistant steel plate has a tensile strength of 1050MPa or more and an elongation A50Not less than 15 percent, the low-temperature impact performance Akv at minus 20 ℃ is not less than 20J, the surface Brinell hardness is not less than 300HB, the cold bending performance is 180 degrees, and D is qualified as 2 a.
5. A method for manufacturing the thin gauge HB300 grade abrasion resistant steel plate as claimed in any one of claims 1-4, characterized in that said manufacturing method comprises rolling; the two-stage controlled rolling process is adopted, the rough rolling accumulated reduction rate is more than or equal to 80 percent, and the finish rolling accumulated reduction rate is more than or equal to 80 percent.
6. The manufacturing method as claimed in claim 5, wherein the rough rolling start temperature is 1100-.
7. The manufacturing method according to claim 5 or 6, further comprising heating: and (3) heating the casting blank in a heating furnace at 1150-1200 ℃ for 2-2.5 h.
8. The manufacturing method according to claim 5 or 6, further comprising cooling, wherein the cooling adopts a three-stage cooling mode, the steel plate after finish rolling is cooled for 1-2s at a cooling speed of more than 80 ℃/s and then is subjected to air cooling, the steel plate is cooled to 650- & gt 700 ℃ after air cooling for 5-8s, then the steel plate is cooled at a cooling speed of more than or equal to 50 ℃/s, the final cooling temperature is controlled to 250- & gt 350 ℃, and finally the steel plate is air cooled to room temperature.
9. The manufacturing method according to claim 5, further comprising smelting and forging, wherein the smelting is performed in a vacuum furnace.
10. The manufacturing method according to claim 5 or 6, wherein the forging is forging the smelted cast slab into a rectangular slab.
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| CN114737128A (en) * | 2022-04-21 | 2022-07-12 | 南京钢铁股份有限公司 | NM 300-grade wear-resistant steel and production method thereof |
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