CN111534744B - Steel for die casting wear-resistant chain plate and manufacturing method thereof - Google Patents
Steel for die casting wear-resistant chain 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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- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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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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- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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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
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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
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
The invention provides a steel for die casting of a wear-resistant chain plate and a manufacturing method thereof, wherein the steel comprises the following components in percentage by weight: c: 0.52-0.68%, Si: less than or equal to 0.40%, Mn: 0.4-1.1%, Cr: less than or equal to 0.50 percent, and less than or equal to 0.5 percent of Nb; al: 0.015 to 0.1 percent of the total weight of the alloy, less than or equal to 0.0015 percent of O, less than or equal to 0.020 percent of impurity element P, less than or equal to 0.010 percent of S, and the balance of Fe and inevitable impurities. The manufacturing method comprises smelting, die casting and hot rolling; the steel plate produced by the invention has the structure of uniform and fine ferrite and pearlite, the volume percentage of the ferrite is 35-45%, the grain size is more than 8.5 grade, the yield strength is 370-470MPa, the surface roughness is less than 1.8um, the hardness after heat treatment is more than 44HRC, various non-metallic inclusions are less than 1.5 grade, the depth of a decarburized layer on the single surface of the steel plate is less than 1.5 percent of the plate thickness, and no grain boundary oxidation exists. The processed chain plate has high wear resistance and the service life is prolonged by more than 50 percent.
Description
Technical Field
The invention belongs to the field of metal materials, and particularly relates to steel for a die casting wear-resistant chain plate and a manufacturing method thereof.
Background
At present, chain plates are mostly processed by 40Mn and 45Mn steel plates, the surface hardness of raw material steel plates is generally required to be 85 HRB-90 HRB so as to ensure the quality of the parts after stamping, the hardness after heat treatment is 38-42HRC, and the problems of chain extension, reduction of the efficiency of a power system, short service life, frequent replacement and the like are caused by easy abrasion deformation in the long-term use process. Especially for some automobile power chains, the service life of the chain directly influences the service life of an automobile engine and even the whole automobile.
The invention discloses a low-carbon microalloyed steel and a method for producing a chain link plate by using the same (99100724.7), and discloses a cold-rolled sheet with low carbon content, high manganese content and high vanadium content for the chain link plate. Low carbon content, low total alloy content, relatively low hardness after heat treatment, insufficient wear resistance and higher cold rolling cost.
The invention relates to a chain steel material (CN103422034A), and the invention relates to a chain plate material of a pipeline chain plate conveyor (CN109881128A), both the invention and the invention add unconventional compounds or elements, need a special production method, and have high cost and complex production process.
The invention discloses steel for circular chain and a manufacturing method thereof (CN102653834A), and discloses mining large-specification high-strength chain steel and a preparation method thereof (CN 201410800419.5). A90-grade chain steel (CN201811242708.2) is an annular chain processed by section bars, the steel for chain has low carbon content, high alloy contents of Ni, Cr, Mo and the like, and high cost, and the conventional heat treatment process cannot meet the requirements of high hardness and high wear resistance of the chain plate.
The outer chain plate of chain (CN 2206868Y) describes the improvement of the shape of chain plate, and does not mention the material.
A caterpillar band steel with high strength, high antiwear nature and long fatigue life and its production process (CN201610507885.3) disclose a round bar rolled from continuous casting square billet, which is not suitable for making chain plate. And the C content is 0.28-0.32%, which is lower, the hardness after heat treatment is difficult to reach more than 37HRC, the Mn content is more than 1.45%, segregation is easy to form, the structure is not uniform, and the fatigue performance is influenced.
The documents of 18MnZL hot rolled strip steel for bicycle chains, chemical component design of steel for racing chains, development and application of steel for cold rolled chain of Wu steel and the like all introduce cold rolled steel plate steel. The 16Mn chain steel introduced in the 16Mn steel chain plate fracture analysis has low carbon content, can meet the hardness requirement after carburization, and has complex process.
The steel grades mentioned in the above documents and inventions are not suitable for directly processing the high-wear-resistant chain plate. Therefore, the invention discloses a die cast steel which is suitable for directly processing various chain plates after cogging and hot rolling into a coiled plate, and has high hardness, good wear resistance and long service life after heat treatment.
Disclosure of Invention
The invention aims to overcome the problems and the defects and provide steel for die casting of a wear-resistant chain plate and a manufacturing method thereof, the steel for the chain plate adopts die casting smelting steel ingots and then rolling coiling plate process, the hardness of the steel plate after heat treatment is more than 40HRC, and the wear-resistant life of the chain is prolonged by more than 50 percent compared with that of a common chain.
The purpose of the invention is realized as follows:
the steel for the die casting wear-resistant chain plate comprises the following components in percentage by weight: c: 0.52 to 0.68 percent, Si: less than or equal to 0.40 percent, Mn: 0.4% -1.1%, Cr: less than or equal to 0.50 percent and less than or equal to 0.5 percent of Nb; al: 0.015 to 0.1 percent of the total weight of the alloy, less than or equal to 0.0015 percent of O, less than or equal to 0.020 percent of impurity element P, less than or equal to 0.010 percent of S, and the balance of Fe and inevitable impurities.
The microstructure of the steel for the die casting wear-resistant chain plate is ferrite and pearlite, the volume percentage of the ferrite is 35-45%, the grain size is more than 8.5 grade, the yield strength is 370-470MPa, the surface roughness is less than 1.8um, various non-metallic inclusions are less than 1.5 grade, and the depth of a decarburized layer on the single surface of the steel plate is less than 1.5 percent of the plate thickness.
The invention has the following design reasons:
c is a main solid solution strengthening element in steel. If the C content is less than 0.52%, it is difficult to ensure the hardness after heat treatment, while if the C content is more than 0.68%, the toughness and plasticity of the steel deteriorate and the chain is liable to brittle fracture. Therefore, the C content is controlled to be 0.52-0.68%.
Mn is a good deoxidizer and desulfurizer, and is an essential element for ensuring the strength and toughness of steel. Manganese and iron form a solid solution, which can increase the hardness and strength of ferrite and austenite in steel. Mn and S are combined to form MnS, so that the influence of hot cracks caused by FeS formed at the grain boundary on the hot formability of the steel for the saw blade is avoided. Meanwhile, Mn is also a good deoxidizer and increases hardenability. The Mn content is too low to meet the requirement of high strength and hardness after heat treatment, and the Mn content is too high to form segregation zones to influence the welding performance and increase the production cost, so the Mn content should be controlled to be 0.4-1.1% by comprehensively considering the factors of cost, performance requirements and the like.
Si is one of common elements in steel and is used as a reducing agent and a deoxidizing agent in the steelmaking process, and Si in a solid solution form can improve the yield strength and the ductile-brittle transition temperature, but if the content of Si exceeds the upper limit, the toughness and the welding performance are reduced. On the other hand, Si is a ferrite forming element, and the high content of Si can cause serious decarburization on the steel surface, so that the content of Si is not easy to be too high, and the content of Si is less than or equal to 0.40 percent.
Cr is an element for remarkably improving the hardenability of steel, a proper amount of Cr is added into the steel to enable a C curve to move to the right, and the spacing between pearlite pieces obtained at the same cooling speed is more refined. For high carbon steel, Cr can increase the activation energy of carbon diffusion and reduce the decarburization tendency of steel. On the other hand, Cr can also increase the ferrite electrode potential, promote the formation of a dense oxide film on the surface of steel, and improve the corrosion resistance. The Cr content is too high, the alloy cost is increased, and the shape of the steel plate is poor and difficult to level, so the Cr content is controlled to be less than or equal to 0.50 percent.
Nb is a micro-alloy element for fine grain strengthening and precipitation strengthening, and the toughness and plasticity of the hot-rolled steel plate and the strength and toughness of the steel after heat treatment can be improved by adding a proper amount of Nb into the steel. Usually, the microalloyed Nb content in the steel is 0.01-0.05%, and the Nb content less than or equal to 0.5% is more than ten times of the normal addition amount in the invention. By adding Nb to steel, fine carbonitride two-phase particles such as NbC and NbCN can be precipitated during hot working, thereby suppressing the deformation recrystallization of austenite, preventing the growth of austenite grains, and refining the grains. The type and size of the generated particles directly influence the service performance of the steel, such as wear resistance and the like. For example, NbC particles smaller than 30um are produced, the effect of grain refinement is obvious, the hardness after heat treatment is obviously improved, the wear resistance is enhanced, and the service life is prolonged. When the length of a timing chain in an engine extends by 50% due to severe wear after a current automobile is used for several years, the engine is judged to be useless. After 0.1-0.5% of Nb is added into the chain steel, the wear resistance is obviously improved, when a common engine is scrapped due to other reasons, the length of the chain is only extended by 20% to the maximum extent, namely, the engine cannot be scrapped due to the problem of abrasion and extension of the timing chain, which is equivalent to prolonging the service life of the engine. On the other hand, Nb can suppress the oxidation and decarburization of the steel surface. Therefore, Nb is controlled to be less than or equal to 0.5 percent.
Al: 0.015-0.1%, Al is generally used as deoxidizer during smelting, crystal grains can be refined, the strength is improved, but Al-containing oxide inclusion is easily formed at the same time, and the fatigue performance of steel is influenced. Therefore, the Al content is controlled to be 0.015-0.10%.
O: o is less than or equal to 0.0015 percent, oxygen is a residual element in steel making, the oxygen content is high, a large amount of non-metallic inclusions exist, and the fatigue performance is seriously influenced. In order to ensure the strength and hardness of the steel for the chain plate after heat treatment, the steel for the chain plate has medium C content and overhigh oxygen content in high-carbon steel, and non-metallic inclusions are not easy to float up during smelting, so that the inclusions in the steel are excessive, and the fatigue life is influenced, therefore, the invention requires that O in a finished steel plate is less than or equal to 0.0015 percent.
P and S are inevitable harmful impurities in steel, and the existence of P and S can seriously deteriorate the toughness of the steel, influence the fatigue performance and shorten the service life. Measures are therefore taken to keep the P and S contents in the steel as low as possible. According to the invention, the maximum P content is limited to 0.020% and the maximum S content to 0.010%.
The above components are designed to have high carbon content, alloy elements such as Mn, Cr, Si and the like are added, the hardenability of the steel plate through hardenability is improved, a certain content of Nb is added, austenite grains are refined to be more than 8.5 grade, the hardness after heat treatment is ensured to be more than 44HRC, and the wear resistance is further improved. The content of impurity elements such as P, S, O and the like is strictly controlled, the fatigue property of steel is improved, and the service life of the chain plate is further prolonged.
The second technical scheme of the invention provides a manufacturing method of the steel for the die casting wear-resistant chain plate, which comprises smelting, die casting and hot rolling;
(1) smelting and die casting:
smelting in an electric furnace, wherein the refining treatment time is required to be more than 30min so that the non-metallic inclusions float sufficiently, the quality of molten steel is ensured, and the fatigue performance of a finished steel plate is improved; casting steel ingots, wherein the O content of the molten steel is required to be less than or equal to 0.0020 percent so as to ensure that the O content of finished products is less than or equal to 0.0015 percent; the size of the steel ingot is not more than 150mm and 150 mm;
an electric furnace is adopted for smelting, the treatment time is more than 30min, the full floating of non-metallic inclusions is facilitated, the purity of molten steel is ensured, and the fatigue performance of a finished steel plate is improved; the O content of the molten steel is required to be less than or equal to 0.0020 percent so as to ensure that the O content of a finished product is less than or equal to 0.0015 percent and various non-metallic inclusions are less than 1.5 grade.
(2) Hot rolling:
(a) cutting off a cap opening after the steel ingot is demoulded, heating to 1100-1250 ℃, preserving heat for 4-6h, keeping the thickness of initial rolling and cogging not more than 100mm, reheating an intermediate billet to 1100-1250 ℃ in a reheating furnace, preserving heat for 0.5-1h, ensuring that the casting billet is heated uniformly, simultaneously reducing surface decarburization as much as possible, inhibiting surface grain boundary oxidation,
(b) the fine and rough rolling adopts high-pressure water for descaling, and the water pressure is more than 15MPa, so that the surface quality of the finished steel plate is ensured;
(c) the first pass reduction rate of rough rolling is more than 30 percent, and the rolling temperature is 1050-1150 ℃;
(d) the total reduction rate of finish rolling is more than 65 percent, and the finish rolling temperature is 720-900 ℃;
(e) after the strip steel is taken out of the finishing mill, the strip steel is cooled to 620-710 ℃ at a cooling speed of more than 10 ℃/S to be coiled so as to control the size of two-phase particles.
The heating temperature of a steel ingot is 1100-1250 ℃, the furnace time is 4-5h, and after the furnace time exceeds 5h, the surface of a casting blank is seriously oxidized and decarburized, so that the surface hardness and the fatigue performance after heat treatment are influenced. In order to control the size of the two-phase particles, the size of the ingot is not more than 150mm x 150mm, so as to promote cooling of the slab, reduce storage energy and inhibit the growth of the two-phase particles. On the other hand, the thickness of the initial billet cannot be larger than 100mm, the intermediate billet is heated back to the heating furnace for the second time to 1100-1250 ℃, and the temperature is kept for 0.5-1h, so that serious surface decarburization oxidation caused by long-time secondary heating is avoided, meanwhile, the solid solution of two-phase particles in the billet is promoted, so that fine two-phase particles are regenerated in the rolling process, the crystal grains are refined to be more than 8.5 grade, the hardness and the wear resistance after heat treatment are improved, and the service life of the chain plate is prolonged. At the temperature of over 1100 ℃, the solid solution speed is obviously increased, the solid solution amount is obviously increased, and after the temperature reaches 1200 ℃, more than 70 percent of Nb is solid-dissolved in the steel.
And (4) cogging and secondarily heating the cast ingot, and rolling by adopting a hot continuous rolling unit. The surface scale is removed by adopting a high-pressure water descaling technology, so that the surface decarburization oxidation of the finished steel plate is reduced, the depth of a single-surface decarburized layer is ensured to be less than 1.5 percent of the plate thickness, no crystal boundary oxidation exists, the surface roughness is below 1.8 mu m, and the surface hardness, wear resistance and fatigue resistance are further improved.
The large reduction rate of the first time which is more than 30 percent is adopted, the final rolling temperature is 720-900 ℃, the austenite region is rolled, the large reduction rate of the first time is adopted, the segregation of the casting blank structure is broken, the banding of the finished product is reduced, and the uniformity of the finished product structure is improved. The total reduction rate of the Nb-containing steel in finish rolling is more than 65%, recrystallization is promoted, a new austenite grain zone is formed, and grains are refined. After rolling, the steel is rapidly cooled to 620-710 ℃ at a cooling speed of more than 10 ℃/S for coiling, so that on one hand, the growth of Nb-containing particles can be inhibited, the particle size is controlled to be below 50 mu m, austenite grains are refined, on the other hand, the surface oxidation and decarburization can be inhibited, and further the surface hardness and the fatigue performance are controlled. The cooling speed is lower than 10 ℃/S, the formed particles are large, and the particles grow obviously after being coiled at the temperature of over 710 ℃. Coiling at a temperature lower than 620 ℃, the steel plate has large brittleness and is easy to break. The grain is larger than 50um, not only can austenite grain not be refined, but also can influence the mechanical property of steel, and the surface of the steel plate is easy to be oxidized and decarburized, the surface grain boundary is seriously oxidized, the surface microcrack is easily formed, and the fatigue property is seriously influenced.
A heat treatment method for steel for die casting wear-resistant chain plates comprises the following steps of processing the steel for the chain plates into semi-finished chain plates, and carrying out heat treatment:
heating at 800-.
The chain plate structure is tempered martensite with the hardness of more than 44 HRC.
The invention has the beneficial effects that:
the steel plate produced by applying the technical scheme disclosed by the invention adopts a die casting production process, austenite grains are fine and uniform, the structure of a hot rolled plate is uniform and fine ferrite and pearlite, the volume percentage of the ferrite is 35-45%, the grain size is above 8.5 grade, the yield strength is 370-470MPa, the surface roughness is below 1.8um, various non-metallic inclusions are less than 1.5 grade, the depth of a decarburized layer on the single surface of the steel plate is less than 1.5 percent of the plate thickness, and the steel plate has no crystal boundary oxidation. The hardness after heat treatment is more than 44HRC, the processed chain plate has high wear resistance, and the service life is prolonged by more than 50%.
Detailed Description
The present invention is further illustrated by the following examples.
According to the embodiment of the invention, smelting, die casting and hot rolling are carried out according to the component proportion of the technical scheme.
(1) Smelting and die casting:
smelting in an electric furnace, wherein the refining treatment time is required to be more than 30 min; casting steel ingots, wherein O in the molten steel is required to be less than or equal to 0.0020 percent; the size of the steel ingot is not more than 150mm and 150 mm;
(2) hot rolling:
(a) cutting off a cap opening after the steel ingot is demoulded, heating to 1100-1250 ℃, preserving heat for 4-6h, keeping the thickness of initial rolling and cogging not more than 100mm, and carrying out secondary heating on the intermediate billet in a reheating furnace to 1100-1250 ℃, preserving heat for 0.5-1 h;
(b) the fine and rough rolling adopts high-pressure water to remove scale, and the water pressure is more than 15 MPa;
(c) the first pass reduction rate of rough rolling is more than 30 percent, and the rolling temperature is 1050-1150 ℃;
(d) the total reduction rate of finish rolling is more than 65 percent, and the finish rolling temperature is 720-900 ℃;
(e) after the strip steel is taken out of the finishing mill, the strip steel is cooled to 620-710 ℃ at a cooling speed of more than 10 ℃/S and is coiled.
A heat treatment method for steel for die casting wear-resistant chain plates comprises the following steps of processing the steel for the chain plates into semi-finished chain plates, and carrying out heat treatment:
heating at 800-
The compositions of the steels of the examples of the invention are shown in table 1. The main process parameters of the steel of the embodiment of the invention are shown in Table 2. The heat treatment process of the steels of the examples of the present invention is shown in Table 3. The properties of the steels of the examples of the invention are shown in Table 4.
TABLE 1 composition (wt%) of steels of examples of the present invention
| Examples | C | Si | Mn | P | S | Cr | Nb | Al | Finished product O |
| 1 | 0.55 | 0.25 | 0.40 | 0.015 | 0.005 | 0.02 | 0.10 | 0.015 | 0.0015 |
| 2 | 0.56 | 0.27 | 0.92 | 0.004 | 0.009 | 0.15 | 0.32 | 0.058 | 0.0012 |
| 3 | 0.68 | 0.08 | 0.91 | 0.008 | 0.02 | 0.22 | 0.015 | 0.029 | 0.0011 |
| 4 | 0.60 | 0.16 | 0.55 | 0.010 | 0.018 | 0.10 | 0.29 | 0.025 | 0.0005 |
| 5 | 0.55 | 0.40 | 0.60 | 0.012 | 0.004 | 0.45 | 0 | 0.078 | 0.0007 |
| 6 | 0.57 | 0.15 | 0.75 | 0.014 | 0.003 | 0.39 | 0 | 0.018 | 0.0008 |
| 7 | 0.59 | 0.16 | 0.88 | 0.013 | 0.008 | 0.50 | 0.35 | 0.055 | 0.00012 |
| 8 | 0.61 | 0.27 | 0.82 | 0.014 | 0.004 | 0.48 | 0.20 | 0.029 | 0.0008 |
| 9 | 0.59 | 0.30 | 0.99 | 0.012 | 0.007 | 0.25 | 0.15 | 0.038 | 0.00010 |
| 10 | 0.53 | 0.08 | 0.68 | 0.010 | 0.01 | 0.14 | 0.09 | 0.045 | 0.0008 |
| 11 | 0.54 | 0.09 | 0.70 | 0.008 | 0.007 | 0.48 | 0.062 | 0.098 | 0.0003 |
| 12 | 0.55 | 0.07 | 0.82 | 0.013 | 0.006 | 0.35 | 0.10 | 0.033 | 0.0009 |
| 13 | 0.54 | 0.16 | 1.08 | 0.013 | 0.008 | 0.25 | 0.25 | 0.035 | 0.0002 |
| 14 | 0.59 | 0.06 | 0.82 | 0.014 | 0.004 | 0.08 | 0.45 | 0.040 | 0.0009 |
| 15 | 0.53 | 0.10 | 0.79 | 0.012 | 0.007 | 0.15 | 0.5 | 0.058 | 0.00010 |
| 16 | 0.60 | 0.18 | 0.88 | 0.030 | 0.01 | 0.46 | 0.36 | 0.055 | 0.00013 |
| 17 | 0.52 | 0.15 | 0.80 | 0.025 | 0.025 | 0.32 | 0.27 | 0.049 | 0.00010 |
| 18 | 0.58 | 0.27 | 0.72 | 0.004 | 0.009 | 0.45 | 0.022 | 0.048 | 0.00012 |
TABLE 2 Main Process parameters of the steels of the examples of the invention
TABLE 3 Heat treatment Process of steels of examples of the invention
TABLE 4 Properties of steels of examples of the invention
In order to express the present invention, the above embodiments are properly and fully described by way of examples, and the above embodiments are only used for illustrating the present invention and not for limiting the present invention, and those skilled in the relevant art can make various changes and modifications without departing from the spirit and scope of the present invention, and any modifications, equivalent substitutions, improvements, etc. made by the persons skilled in the relevant art should be included in the protection scope of the present invention, and the protection scope of the present invention should be defined by the claims.
Claims (1)
1. The steel for the die casting wear-resistant chain plate is characterized by comprising the following components in percentage by weight: c: 0.52% -0.68%, Si: less than or equal to 0.40 percent, Mn: 0.4% -1.1%, Cr: 0.15-0.50% of Nb, 0.36-0.5% of Nb; al: 0.055% -0.1%, less than or equal to 0.0015% of O, less than or equal to 0.020% of impurity element P, less than or equal to 0.010% of S, and the balance of Fe and inevitable impurities; the Nb particle size in the steel is less than 50 um;
the microstructure of the steel for the die casting wear-resistant chain plate is ferrite and pearlite, the ferrite volume accounts for 35-45%, the grain size is more than 8.5 grade, the yield strength is 370-470MPa, the surface roughness is less than 0.98 mu m, various non-metallic inclusions are less than 1.5 grade, and the depth of a decarburized layer on the single-side surface of the steel plate is less than 1.5 percent of the plate thickness;
the manufacturing method of the steel for the die casting wear-resistant chain plate comprises smelting, die casting and hot rolling;
(1) smelting and die casting:
smelting in an electric furnace, wherein the refining treatment time is required to be more than 30 min; casting steel ingots, wherein O in the molten steel is required to be less than or equal to 0.0020 percent; the size of the steel ingot is not more than 150mm and 150 mm;
(2) hot rolling:
(a) cutting off a cap opening after the steel ingot is demoulded, heating to 1100-1250 ℃, preserving heat for 4-6 hours, keeping the thickness of initial rolling and cogging not more than 100mm, and carrying out secondary heating on an intermediate billet in a reheating furnace to 1100-1250 ℃, preserving heat for 0.5-1 hour;
(b) the fine and rough rolling adopts high-pressure water to remove scale, and the water pressure is more than 15 MPa;
(c) the first pass reduction rate of rough rolling is more than 30%, and the initial rolling temperature is 1050-1150 ℃;
(d) the total reduction rate of finish rolling is more than 65%, and the finish rolling temperature is 720-899 ℃;
(e) after the strip steel is discharged from the finishing mill, cooling the strip steel to 680-710 ℃ at a cooling speed of 10-48 ℃/s and coiling the strip steel;
after the steel for the chain plate is processed into a semi-finished product of the chain plate, heat treatment is carried out, and the specific process comprises the following steps:
heating to 800-825 ℃, preserving the heat for 15-27 min, and then performing oil quenching, wherein the temperature of quenching oil is not higher than 80 ℃, cooling to below 200 ℃, and feeding into a furnace for tempering, wherein the tempering temperature is 300-400 ℃;
the chain plate structure prepared after the heat treatment process is tempered martensite with the hardness of more than 44 HRC.
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