CN111394639A - Manufacturing method of high-wear-resistance gear steel - Google Patents
Manufacturing method of high-wear-resistance gear steel 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
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/002—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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- 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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- 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
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
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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
- C21D2211/009—Pearlite
Abstract
The invention relates to a manufacturing method of high-wear-resistance gear steel, which comprises the following steps of (1) smelting: the molten steel comprises the following components: 0.15-0.60%, Si: 0.50 to 1.3%, Mn: 0.50-1.2%, Cr: 0.60-1.5%, P: less than or equal to 0.030 percent, S: less than or equal to 0.035%, Al: 0.010-0.050%, N: 0.008-0.025%, and the balance of Fe; (2) pouring: casting the molten steel into a steel billet; (3) rolling: heating a steel billet and then rolling in a single-phase region: the initial rolling temperature is 980-1100 ℃, and the middle rolling, the pre-finish rolling and the finish rolling are sequentially carried out; performing controlled cooling in the rolling process, performing water mist cooling after the billet is subjected to medium rolling, performing pre-finish rolling, performing water mist cooling again, performing KOCKS finish rolling, and controlling the finish rolling temperature to be 780-900 ℃ to obtain unstable austenite; (4) and (3) cooling: and (3) blowing the blank on a cooling bed for cooling, controlling the average cooling speed to be 40-80 ℃/min and the final cooling temperature to be 300-480 ℃, air-cooling the material to room temperature after final cooling, and converting austenite into ferrite and pearlite in the cooling process. The steel has excellent wear resistance after carburization quenching and tempering.
Description
Technical Field
The invention relates to a manufacturing method of wear-resistant steel, in particular to a manufacturing method of wear-resistant steel with high silicon content.
Background
Recently, with the development of industries such as automobiles, it is one of the important development directions for improving the design wear life of gears and increasing the stability and life of operating equipment, thereby improving efficiency and reducing cost. From the design point of view of the gear, the surface is required to have high hardness to improve wear resistance, and the core has certain toughness. The gear steel is usually designed by adopting medium and low carbon, the toughness of a core part is ensured, and one or more alloy elements of Cr, Mo, V and B are added to improve the hardenability of the material. And during subsequent heat treatment, the material is subjected to surface carburization (actually, carburization, nitridation or carbonitriding can be performed, and the carburization is collectively expressed herein), so that the wear resistance of the surface is remarkably improved, and the toughness of the core part can be ensured. The case carburizing treatment is usually carried out under a high temperature condition for a long time. The silicon can obviously improve the ferrite strength so as to improve the strength and the hardness of steel, and after the material is subjected to subsequent carburizing, quenching and tempering, the wear resistance of the material can be greatly improved due to the existence of silicide in a hardening layer. However, silicon is an easily oxidizable element and easily segregates at grain boundaries, which easily causes oxidation of the grain boundaries of silicon during the conventional carburizing heat treatment process, thus deteriorating the gear performance. In order to prevent the oxidation of crystal boundary caused by surface carburization, the traditional gear adopts a design of medium and low silicon. However, with the improvement of the technology and the progress of the tooling equipment, the adoption of vacuum carburization or protective atmosphere can effectively avoid the oxidation of the grain boundary caused by silicon. At the moment, the high-silicon design is adopted, so that the wear resistance of the gear can be obviously improved, crystal boundary oxidation is not caused, and the wear resistance of the gear is several times of that of the traditional low-silicon design. And silicon is a relatively cheap alloy element, and the high-silicon design can properly reduce the addition of other alloy elements, thereby being beneficial to reducing the production cost of materials. In conclusion, the high-silicon high-wear-resistance gear steel has wide market prospect.
Disclosure of Invention
The invention aims to provide a method for manufacturing more wear-resistant gear steel by adopting a component design for increasing the content of Si. The hot rolled structure of the steel is ferrite plus pearlite. Because of the need of carburizing treatment in gear processing, the invention aims to ensure that the material has excellent wear resistance after carburizing, quenching and tempering, i.e. the contact fatigue life is long
The technical scheme of the invention is as follows: the manufacturing method of the high wear-resistant gear steel comprises the following steps
(1) Smelting: the molten steel comprises the following components in percentage by mass: 0.15-0.60%, Si: 0.50 to 1.3%, Mn: 0.50-1.2%, Cr: 0.60-1.5%, P: less than or equal to 0.030 percent, S: less than or equal to 0.035%, Al: 0.010-0.050%, N: 0.008-0.025%, and the balance of Fe and inevitable impurity elements;
(2) pouring: adopting advanced tail end electromagnetic stirring and soft reduction advanced equipment working procedures, controlling the casting superheat degree at 10-40 ℃, and casting the molten steel into a steel billet;
(3) rolling: reheating the steel billet to complete austenitization, taking out of the furnace, descaling by high-pressure water, and then carrying out single-phase region rolling: the initial rolling temperature is 980-1100 ℃, and the medium rolling, the pre-finish rolling and the finish rolling are sequentially carried out by adopting 12 two-roll mills and 5 KOCKS three-roll mills; the controlled cooling is carried out in the rolling process, the water mist cooling is carried out after the billet is rolled in the middle, the water mist cooling is carried out again after the billet is rolled in advance, then the billet enters KOCKS finish rolling, the finish rolling temperature is controlled to be 780-900 ℃, unstable austenite can be obtained by controlling the lower finish rolling temperature, the unstable austenite can be obtained by combining the controlled cooling in the rolling process, the unstable austenite is reduced, the transformation trend of the austenite is improved, the phase change of the austenite in the cooling link is promoted, the phase change can be rapidly carried out under the air cooling condition, the water cooling is not needed for cooling, the risk of uneven tissue caused by supercooling is reduced, the residual stress is obviously reduced, and the fatigue performance of the steel after carburization quenching and tempering is extremely favorable.
(4) And (3) cooling: and after rolling, blowing the blank on a cooling bed for cooling, controlling the average cooling speed to be 40-80 ℃/min (equivalent to 0.67-1.33 ℃/s), reducing the banded structure of the rolled material, improving the uniformity of the structure, controlling the final cooling temperature to be 300-480 ℃, air-cooling the material to room temperature after final cooling, and smoothly converting all austenite into ferrite and pearlite in the cooling process.
Preferably, in addition to precisely controlling the composition of molten steel when smelting the steel, it is important to improve the purity of molten steel, and the higher the purity is, the more advantageous the improvement of the contact fatigue life of steel. In order to improve the purity of steel, molten iron selected for steelmaking needs to be subjected to desulfurization and dephosphorization treatment in advance. High-purity high-quality alloy is used in converter or electric furnace smelting, and deoxidation is enhanced in the molten steel refining process to improve the yield of silicon.
Preferably, the steel billet in the step (3) is reheated by a stepping heating furnace, the temperature of the preheating section is controlled to be 760-860 ℃, the temperature of the first heating section is controlled to be 960-1060 ℃, the temperature of the second heating section is controlled to be 1050-1180 ℃, the temperature of the soaking section is controlled to be 1080-1200 ℃, the billet is fully and uniformly heated, and the total heating time is 2.5 hours or more.
The design principle of each element of the steel material is as follows:
si: 0.50 to 1.3 percent. This element is a key, core element of the present invention. Si can obviously improve the ferrite strength so as to improve the strength and the hardness of steel, and meanwhile, silicon is an easily-oxidized element and is easily segregated at a grain boundary, so that the grain boundary of silicon is easily oxidized in the traditional carburizing heat treatment process, and the performance of the gear is deteriorated. In order to prevent the oxidation of crystal boundary caused by surface carburization, the traditional gear adopts a design of medium and low silicon. However, with the improvement of the technology and the progress of the tooling equipment, the crystal boundary oxidation caused by silicon can be effectively avoided by adopting vacuum carburization or protective atmosphere. At the moment, the high-silicon design is adopted, so that the wear resistance of the gear can be obviously improved, crystal boundary oxidation is not caused, and the wear resistance of the gear is several times of that of the traditional low-silicon design. And silicon is a relatively cheap alloy element, and the high-silicon design can properly reduce the addition of other alloy elements, thereby being beneficial to reducing the production cost of materials. The steel material of the present invention is designed to be high silicon, so that the Si range is set to 0.50 to 1.3%, and the Si content is preferably 0.80 to 1.2%.
C: 0.15 to 0.60 percent. The element is one of the key elements of the invention, the steel grade of the invention is a ferrite plus pearlite structure in a hot rolling state, and after processing and carburizing and quenching tempering heat treatment, the surface is required to be a hardening layer with high hardness, and the core part is required to have better toughness and is a non-hardening structure. In order to blend the above properties, the steel material of the present invention has a C content of 0.15 to 0.60%, preferably 0.18 to 0.40%.
P: less than or equal to 0.030 percent. P tends to undergo severe microsegregation during casting solidification and then aggregates at grain boundaries during heating, increasing the brittleness, particularly cold brittleness, of the steel, and deteriorating the cold forgeability of the material. The P content of the steel material in the present invention is set to 0.030% or less, and preferably 0.020% or less.
S: less than or equal to 0.035%. S is a free-cutting element. When a certain amount of Mn is contained in the steel, MnS or a MnS-containing complex is easily formed, thereby improving the machinability of the material. However, sulfides generally have a low melting point and an excessively high S content, so that the material has a hot brittle effect and an increased tendency to decarburization. In order to fully exert the above effects, the S content of the steel material of the present invention is set to 0.035% or less, and the S content is preferably 0.005 to 0.025%.
In order to meet the comprehensive properties of strength, hardness, hardenability and the like of the material, the following main alloy elements are added into the steel.
Mn: 0.50 to 1.2 percent. Mn is used as an element of the deoxidizer action, the strength of the steel can be improved on the basis of not obviously influencing the plasticity of the material by proper amount of Mn, and the addition of a certain amount of Mn is very important for ensuring the mechanical property of the material. In addition, Mn combines S and the like in the steel to form sulfides, and the sulfides have good plasticity, exert a notch effect during cutting and improve the cutting performance of the material. In order to fully exert the above effects, the Mn content of the steel material of the present invention is set to 0.50 to 1.2%, and the Mn content is preferably 0.70 to 1.0%.
N: 0.008 to 0.025 percent. N is used as an additive element and is preferentially combined with Al in steel to generate dispersed and fine aluminum nitride, so that the growth of crystal grains of the material during carburization can be effectively prevented. The amount of N added is determined according to the amount of Al added, and Al/N is usually 1.5 to 2.5. The content of N in the steel material is set to 0.008-0.025%, and the content of N is preferably 0.010-0.020%.
Cr: 0.60 to 1.5 percent. Cr element increases hardenability, thins the lamellar spacing of pearlite, and is beneficial to improving the formation proportion of a fine lamellar pearlite structure and the uniformity of a microstructure, thereby effectively improving the properties of the material such as strength, fatigue and the like. The Cr content of the steel material of the present invention is set to 0.60 to 1.5%, preferably 0.90 to 1.20%.
Al: 0.010-0.050%. Al is used as a deoxidizing element, and AlN formed by combining with N and the like in steel can effectively prevent austenite grains from coarsening and plays a role in preventing grain growth. However, the content of Al is too high, and Al is easily formed2O3Or containing Al2O3Composite inclusions, thereby deteriorating material properties, particularly fatigue properties. In order to fully exert the above effects, the Al content of the steel material in the present invention is set to 0.010 to 0.050%. The Al content is preferably 0.020-0.040%.
The gear steel designed by the invention can also be added with one or more alloy elements such as Mo, Ni, B and the like in order to adjust the hardenability. Meanwhile, in order to prevent the grain coarsening of the material in the carburizing process, one or more alloy elements such as Nb, Ti, V and the like can be added to refine the grains.
Compared with the prior art, the invention has the advantages that:
the invention particularly adds Si with higher content, and the Si can properly improve the content of the residual austenite in the quenched and tempered steel, thereby improving the toughness of the steel, effectively absorbing the thermal stress and the mechanical stress of the gear operation and eliminating the stress concentration. After gear quenching, if the toughness is too low, the tooth surface is easily micro-peeled and gradually expanded under repeated loading force, and finally the contact fatigue life of the gear is reduced, that is, the wear resistance is reduced. The existence of a proper amount of residual austenite among the martensite laths plays a role in segmenting and refining the martensite laths, and is beneficial to improving the strength and the toughness of the steel. Si is a non-carbide forming element, and is enriched around carbon in the tempering process to prevent carbon atoms from continuously diffusing in ferrite, thereby preventing the growth and coarsening of carbide. Si can replace part of iron atoms to be dissolved in the alpha iron crystal lattice, so that the tempering stability of the steel is improved.
The gear steel obtained by the preparation method has a uniform ferrite plus pearlite metallographic structure, the yield strength is more than or equal to 680MPa, the tensile strength is more than or equal to 900MPa, the elongation is more than or equal to 12 percent, and the surface shrinkage is more than or equal to 40 percent. The contact fatigue life of the wear-resisting test sample made of the steel is 3.8 times of that of the traditional gear steel. The steel material has excellent wear resistance after carburization quenching and tempering, namely, the contact fatigue life is long.
Drawings
FIG. 1 is a 100-fold metallographic photograph of a steel for a gear in example 1 of the present invention;
FIG. 2 is a 500-fold metallographic photograph of a steel for a gear in example 1 of the present invention;
FIG. 3 is a graph of the shape of a contact fatigue specimen in an example of the invention.
Detailed Description
The invention is described in further detail below with reference to the accompanying examples.
Examples 1 to 3
The manufacture of the steel for gears was carried out as follows:
1) smelting: the method comprises the following steps of carrying out molten iron pretreatment on 100 tons of iron ladles, then carrying out external refining after smelting in a 100 tons of steel making furnace, carrying out strong deoxidation by adopting silicon carbide and an aluminum wire in the refining process, accurately regulating and controlling main chemical elements during refining, carrying out vacuum degassing treatment on molten steel to remove H, regulating N to a target range, and removing light impurities to purify the molten steel.
2) Continuous casting, namely, continuously casting a 240mm × 240mm square billet, controlling the superheat degree of a tundish to be 10-40 ℃, controlling the segregation of materials, and adopting advanced tail end electromagnetic stirring and continuous casting soft reduction advanced equipment and process during continuous casting, wherein the chemical component percentage of the obtained continuous casting billet is shown in the following table 1:
table 1 (wt.%, balance Fe and other unavoidable impurity elements)
| Serial number | C | Si | Mn | P | S | Cr | Al |
| 1 | 0.20 | 0.80 | 0.88 | 0.015 | 0.025 | 0.95 | 0.035 |
| 2 | 0.18 | 0.90 | 0.85 | 0.012 | 0.018 | 1.12 | 0.034 |
| 3 | 0.40 | 1.15 | 0.90 | 0.009 | 0.020 | 1.17 | 0.029 |
3) Heating: the blank is heated in a stepping heating furnace and comprises a preheating section, a first heating section, a second heating section and a soaking section, wherein the temperature of the preheating section is controlled to be 760-860 ℃, the temperature of the first heating section is controlled to be 960-1060 ℃, the temperature of the second heating section is controlled to be 1050-1180 ℃, the temperature of the soaking section is controlled to be 1080-1200 ℃, the total heating time is more than 2.5 hours, and high-pressure water descaling is performed after the blank is taken out of the furnace.
4) Hot rolling: the initial rolling temperature is 980-1100 ℃, the final rolling temperature is 780-900 ℃, the rolling is carried out in a single-phase region, the maximum rolling reduction of a single pass is controlled to be 20-30 mm, a 12-frame two-roller mill and a 5-frame KOCKS three-roller mill are adopted for rolling, the cooling is controlled in the rolling process, the material is subjected to water mist weak cooling after being rolled out of the middle, then the material is subjected to pre-finish rolling, the material is subjected to water mist cooling again after being rolled out of the pre-finish rolling, the cooling strength is properly improved at the moment, and the material enters the KOCKS finish rolling and.
5) And (3) cooling: and transferring the steel to a cooling bed, carrying out blast cooling, controlling the average cooling speed at 50-80 ℃/min and the final cooling temperature at 300-480 ℃, and then carrying out air cooling to room temperature.
The specific process parameters for each example are shown in table 2 below:
TABLE 2 (specific Process parameters for heating, Hot Rolling, Cooling)
The steel for gears in examples 1 to 3 was tested, and the measured contact fatigue life and mechanical properties are shown in table 3 below:
TABLE 3
Note: the contact fatigue test sample is subjected to carburization and quenching tempering, then is sampled, processed and tested according to the instruction attached figure 3, the test is carried out according to YB-T5345-7The average cycle number of the comparative steel grade 20MnCr5 was 1.7 x 10 under the same test conditions7The cycle times of the gear steel of the embodiment are 3.8 times of those of the comparative steel grade. The test results are in table 3.
As can be seen from Table 3, the mechanical properties in the examples completely meet the design requirements, which indicate that the yield strength of the material is greater than or equal to 680MPa, the tensile strength is greater than or equal to 900MPa, the elongation is greater than or equal to 12%, and the surface shrinkage is greater than or equal to 40%. The contact fatigue performance of the steel after carburizing and quenching is obvious. Has excellent wear resistance and belongs to high-wear-resistance gear steel.
Fig. 1 and 2 show the microstructure of the steel for a gear of example 1. As can be seen from the figure, the microstructure of the steel for gears was uniform ferrite + pearlite and was very uniform.
Although preferred embodiments of the present invention have been described in detail hereinabove, it should be clearly understood that modifications and variations of the present invention are possible to those skilled in the art. 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 (9)
1. A manufacturing method of high wear-resistant gear steel is characterized by comprising the following steps: comprises the following steps
(1) Smelting: the molten steel comprises the following components in percentage by mass: 0.15-0.60%, Si: 0.50 to 1.3%, Mn: 0.50-1.2%, Cr: 0.60-1.5%, P: less than or equal to 0.030 percent, S: less than or equal to 0.035%, Al: 0.010-0.050%, N: 0.008-0.025%, and the balance of Fe and inevitable impurity elements;
(2) pouring: casting the molten steel into a steel billet;
(3) rolling: reheating the steel billet to complete austenitization, taking out of the furnace, descaling by high-pressure water, and then carrying out single-phase region rolling: the initial rolling temperature is 980-1100 ℃, and the middle rolling, the pre-finish rolling and the finish rolling are sequentially carried out; performing controlled cooling in the rolling process, performing water mist cooling after the billet is subjected to medium rolling, performing pre-finish rolling, performing water mist cooling again, performing KOCKS finish rolling, and controlling the finish rolling temperature to be 780-900 ℃, wherein unstable austenite can be obtained at a lower finish rolling temperature;
(4) and (3) cooling: and after rolling, blowing the blank on a cooling bed for cooling, controlling the average cooling speed to be 40-80 ℃/min, reducing the banded structure of the rolled material, improving the uniformity of the structure, controlling the final cooling temperature to be 300-480 ℃, air-cooling the material to room temperature after final cooling, and converting austenite into ferrite and pearlite in the cooling process.
2. The method for manufacturing high wear-resistant gear steel according to claim 1, wherein the step (1) of smelting comprises L F furnace refining of the molten steel, and deoxidation is enhanced in the refining process to improve the yield of silicon.
3. The method for manufacturing a highly wear-resistant gear steel according to claim 1, wherein: and (3) controlling the degree of superheat of pouring in the step (2) to be 10-40 ℃.
4. The method for manufacturing a highly wear-resistant gear steel according to claim 1, wherein: and (3) heating the steel blank by adopting a stepping heating furnace, wherein the temperature of a preheating section is controlled to be 760-860 ℃, the temperature of a first heating section is controlled to be 960-1060 ℃, the temperature of a second heating section is controlled to be 1050-1180 ℃, the temperature of a soaking section is controlled to be 1080-1200 ℃, the steel blank is fully and uniformly heated, and the total heating time is 2.5 hours or more.
5. The method for manufacturing a highly wear-resistant gear steel according to claim 1, wherein: and (4) rolling by adopting 12 two-roll mills and 5 KOCKS three-roll mills.
6. The method for manufacturing a highly wear-resistant gear steel according to claim 1, wherein: the content of Si in the step (1) is 0.8-1.2%.
7. The method for manufacturing a highly wear-resistant gear steel according to claim 1, wherein: c in the step (1): 0.18 to 0.40%, Mn: 0.70-1.0%, Cr: 0.90-1.2%, P: less than or equal to 0.020%, S: 0.005-0.025%, Al: 0.020 to 0.040%, N: 0.010-0.020%.
8. The method for manufacturing a highly wear-resistant gear steel according to claim 1, wherein: the molten steel in the step (1) also contains one or more of Nb, Ti and V, the sum of the addition of Nb, Ti and V is not higher than 0.08%, and the addition of Ti is not higher than 0.02%.
9. The method for manufacturing a highly wear-resistant gear steel according to claim 1, wherein: the molten steel in the step (1) also contains one or more of Mo, Ni and B.
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
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| CN112522632A (en) * | 2020-12-09 | 2021-03-19 | 苏州莱特复合材料有限公司 | Powder metallurgy wear-resistant stator and production process thereof |
| CN112779468A (en) * | 2020-12-16 | 2021-05-11 | 石家庄钢铁有限责任公司 | High-performance steel for automobile gear and production method thereof |
| CN112941404A (en) * | 2021-01-18 | 2021-06-11 | 江阴兴澄特种钢铁有限公司 | High-strength high-toughness low-carbon gear steel and preparation method thereof |
| CN113481427A (en) * | 2021-04-13 | 2021-10-08 | 江阴兴澄特种钢铁有限公司 | Medium-carbon low-alloy CrMnSiB series steel forging and rolling bar for producing cold heading module by continuous casting billet and manufacturing method thereof |
| CN115125430A (en) * | 2022-05-23 | 2022-09-30 | 江苏永钢集团有限公司 | Nitrogen-containing wind power gear steel and nitrogen increasing method thereof |
| CN115449700A (en) * | 2022-09-20 | 2022-12-09 | 西安建筑科技大学 | Method for improving low-carbon gear steel strip-shaped structure based on oxide metallurgy and low-carbon gear steel |
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| CN112442635A (en) * | 2020-11-13 | 2021-03-05 | 唐山钢铁集团高强汽车板有限公司 | High-performance low-alloy high-strength steel plate with strength of above 800MPa and preparation method thereof |
| CN112522632A (en) * | 2020-12-09 | 2021-03-19 | 苏州莱特复合材料有限公司 | Powder metallurgy wear-resistant stator and production process thereof |
| CN112779468A (en) * | 2020-12-16 | 2021-05-11 | 石家庄钢铁有限责任公司 | High-performance steel for automobile gear and production method thereof |
| CN112941404A (en) * | 2021-01-18 | 2021-06-11 | 江阴兴澄特种钢铁有限公司 | High-strength high-toughness low-carbon gear steel and preparation method thereof |
| CN112941404B (en) * | 2021-01-18 | 2022-07-15 | 江阴兴澄特种钢铁有限公司 | High-strength high-toughness low-carbon gear steel and preparation method thereof |
| CN113481427A (en) * | 2021-04-13 | 2021-10-08 | 江阴兴澄特种钢铁有限公司 | Medium-carbon low-alloy CrMnSiB series steel forging and rolling bar for producing cold heading module by continuous casting billet and manufacturing method thereof |
| CN115125430A (en) * | 2022-05-23 | 2022-09-30 | 江苏永钢集团有限公司 | Nitrogen-containing wind power gear steel and nitrogen increasing method thereof |
| CN115449700A (en) * | 2022-09-20 | 2022-12-09 | 西安建筑科技大学 | Method for improving low-carbon gear steel strip-shaped structure based on oxide metallurgy and low-carbon gear steel |
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