CN116083801A - High-uniformity high-mirror polishing performance die steel and preparation method thereof - Google Patents
High-uniformity high-mirror polishing performance die steel and preparation method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 161
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- 239000002699 waste material Substances 0.000 description 1
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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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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/84—Controlled slow cooling
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- C21D6/00—Heat treatment of ferrous alloys
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
- C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
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- C22B9/18—Electroslag remelting
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
The invention discloses high-uniformity high-mirror polishing die steel and a preparation method thereof, belongs to the technical field of tool die steel, and solves the problems of serious carbide segregation and poor tissue uniformity of plastic die steel in the prior art. The high-uniformity high-mirror polishing performance die steel comprises the following components in percentage by mass: c:0.10 to 0.30 percent, si: less than or equal to 1 percent, mn: less than or equal to 1 percent, cr:10.0 to 14.0 percent of Ni:0.2 to 2.0 percent, mo:0.5 to 1.0 percent, V:0.005% -1.00%, N:0.15 to 0.50 percent, and the balance of Fe and unavoidable impurities. The die steel with high uniformity and high mirror polishing performance has good uniformity, excellent cutting performance and excellent corrosion resistance.
Description
Technical Field
The invention relates to the technical field of tool and die steel, in particular to die steel with high uniformity and high mirror polishing performance and a preparation method thereof.
Background
The corrosion-resistant plastic die steel is used as a high-end product in the die steel, is mainly used for forming special engineering plastics with higher temperature and plastics containing flame retardants, and can decompose and generate a large amount of corrosive gases such as hydrogen chloride, hydrogen fluoride, sulfur dioxide and the like in a molten state to generate corrosion action on a used plastic die cavity, so that the service life of the die is reduced. Therefore, such a mold should have a certain corrosion resistance. The corrosion-resistant plastic die steel commonly used at present is 4Cr13, 9Cr18 and the like, and belongs to martensitic stainless steel. However, the steel still has the problems of serious carbide segregation, poor structure uniformity, insufficient corrosion resistance and the like, and is difficult to meet the requirements of ultra-high precision plastic products on high polishing performance and corrosion resistance, so that the quality stabilization and market improvement of the steel are restricted, and the performance of the steel still needs to be further improved.
Disclosure of Invention
In view of the above, the present invention aims to provide a high-uniformity high-mirror polishing performance die steel and a preparation method thereof, which are used for solving the problems of serious carbide segregation and poor tissue uniformity of the existing high-nitrogen corrosion-resistant plastic die steel; the hardness, the corrosion resistance and the wear resistance cannot be simultaneously considered.
The aim of the invention is mainly realized by the following technical scheme:
the invention provides high-uniformity high-mirror polishing performance die steel, which comprises the following components in percentage by mass: c:0.10 to 0.30 percent, si: less than or equal to 1 percent, mn: less than or equal to 1 percent, cr:10.0 to 14.0 percent of Ni:0.2 to 2.0 percent, mo:0.5 to 1.0 percent, V:0.005% -1.00%, N:0.15 to 0.50 percent, and the balance of Fe and unavoidable impurities.
Further, the components of the die steel with high uniformity and high mirror polishing performance are further added with one or more elements selected from the following elements in percentage by mass: cu is less than or equal to 0.5 percent, nb is less than or equal to 0.05 percent, co is less than or equal to 0.5 percent, and rare earth element is less than or equal to 0.05 percent.
Further, the high-uniformity high-mirror polishing performance die steel comprises the following components in percentage by mass: c:0.11 to 0.30 percent, si:0.20 to 0.80 percent of Mn:0.20 to 0.80 percent, cr:10.2 to 13.7 percent of Ni:0.2 to 1.9 percent of Mo:0.5 to 1.0 percent, V:0.005% -0.95%, N:0.15 to 0.50 percent, and the balance of Fe and unavoidable impurities.
The invention also provides a preparation method of the high-uniformity high-mirror-finish-performance die steel, which is used for preparing the high-uniformity high-mirror-finish-performance die steel and comprises the following steps:
step 1, smelting and pouring to obtain an electrode blank, and carrying out slow cooling or heat preservation annealing treatment on the electrode blank;
step 2, remelting the electrode blank by a pressurizing electroslag furnace, casting into a steel ingot, and carrying out slow cooling or heat preservation annealing treatment on the steel ingot;
step 3, forging the steel ingot to obtain a forging stock;
step 4, performing dispersion treatment on the forging stock;
step 5, annealing the steel subjected to the dispersion treatment;
step 6, quenching the annealed steel, and tempering; or quenching the annealed steel, performing deep cooling treatment, and then performing tempering treatment.
Further, in step 3, forging includes: fully heating and preserving heat of the steel ingot, and forging; the heating temperature is controlled to 1160-1200 ℃, and the heat preservation time is 10-15 h.
In the step 3, the initial forging temperature is 1160-1200 ℃, and the final forging temperature is 830-860 ℃.
Further, in step 4, the dispersion treatment includes: heating the forging stock to 980-1020 ℃ for heat preservation for 1-2 h, and then cooling to room temperature; then preserving heat for 2-4 hours at the temperature of 630-670 ℃ for the second time, and cooling to room temperature.
Further, in step 5, the annealing treatment includes: heating the steel subjected to the dispersion treatment to 850+/-10 ℃, and preserving heat for 1-2 hours; furnace cooling to 650+/-10 ℃, preserving heat for 1-2 h, and then discharging after furnace cooling to below 400 ℃.
In step 6, tempering is performed at 150-520 ℃.
Further, in the step 6, the structure of the tempered steel material is martensite+fine dispersed carbide and carbonitride precipitated phases, the martensite laths are uniform, and no obvious network segregation and stripe segregation are seen.
Compared with the prior art, the invention has the following beneficial effects:
a) The die steel with high uniformity and high mirror polishing performance reduces carbide and tissue segregation by adopting low C and adding a proper amount of Cr, mo, V and N elements, and obtains the structure of martensite, tiny dispersed carbide and carbonitride precipitated phases under a proper dispersion treatment and quenching and tempering process, wherein martensite laths are uniform, no obvious net segregation and stripe segregation are seen, so that the die steel with high uniformity and high mirror polishing performance and excellent corrosion resistance is obtained.
b) The die steel with high uniformity and high mirror polishing performance prepared by the components and the method has good comprehensive mechanical properties, and the annealed steel has good uniformity and excellent cutting performance. The tempered steel has uniform structure, higher tempering hardness, higher impact toughness and lower roughness, meets the requirements of mirror polishing performance, and has excellent corrosion resistance.
Additional features and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention. The objectives and other advantages of the invention will be realized and attained by the structure particularly pointed out in the written description and claims thereof as well as the appended drawings.
Drawings
The drawings are only for purposes of illustrating particular embodiments and are not to be construed as limiting the invention, like reference numerals being used to refer to like parts throughout the several views.
FIG. 1 is a tempered structure of example 2, 50X;
FIG. 2 is a drawing of tempered structure of comparative example 1 at 100X;
FIG. 3 is a drawing showing a tempered structure of 500X after tempering at 240 ℃ in the steel of example 1;
FIG. 4 is a drawing showing a tempered structure of 500X after tempering at 240 ℃ in the steel of comparative example 1;
FIG. 5 is a drawing showing a tempered structure of 500X after tempering at 500 ℃ in the steel of example 1;
fig. 6 is a drawing showing a tempered structure of 500× after tempering at 500 ℃.
Detailed Description
Preferred embodiments of the present invention are described in detail below with reference to the attached drawing figures, which form a part of the present invention and are used in conjunction with embodiments of the present invention to illustrate the principles of the present invention.
The invention provides high-uniformity high-mirror polishing performance die steel, which comprises the following components in percentage by mass: c:0.10 to 0.30 percent, si: less than or equal to 1 percent, mn: less than or equal to 1 percent, cr:10.0 to 14.0 percent of Ni:0.2 to 2.0 percent, mo:0.5 to 1.0 percent, V:0.005% -1.00%, N:0.15 to 0.50 percent, and the balance of Fe and unavoidable impurities.
The following is a specific description of the action and the selection of the amounts of the components contained in the invention:
c: the carbon content in the steel determines the hardness of the matrix of the steel, and for tool and die steels, one part of carbon is dissolved into the matrix to play a solid solution strengthening role, and the other part of carbon is combined with a strong carbide forming element to form alloy carbide. The C and some alloy elements form alloy carbide to improve the hardness and wear resistance of the steel, and the evenly dispersed alloy carbide and tempered martensite structure affect the corrosion resistance of the steel. In order to obtain higher hardness, wear resistance and corrosion resistance, the carbon content is controlled to be 0.10-0.30 percent in the invention.
Si: silicon is added as a reducing agent and a deoxidizing agent in the steelmaking process, which has an obvious effect on improving corrosion resistance, however, too high a content of Si not only causes a decrease in toughness of steel but also promotes generation of segregation, so that the content of silicon is generally controlled to be 1% or less.
Mn: manganese is an element for improving the hardenability of steel, so that the core can achieve the desired mechanical properties. The proper amount of manganese can also effectively improve the strength, hardness and toughness of the steel, eliminate the harmful effects of sulfur and oxygen on the steel, improve the hot processing performance of the steel and improve the cold embrittlement tendency of the steel. However, since segregation is likely to occur when the Mn content is too high, the Mn content in the present invention is controlled to be 1.0% or less.
Ni: nickel is an important hardenability enhancing element that can improve the strength and toughness of steel in some steels. The addition of Ni can improve the passivation tendency of Fe-Cr alloy, not only can improve the corrosion resistance of steel in acid and alkali mediums, but also has the corrosion resistance to atmosphere and salt. The Ni content in the steel of the invention is 0.2% -2.0%.
Cr: chromium is used as a main constituent element of the corrosion resistant steel, so that not only can the hardenability of Fe-Cr alloy be improved, but also the corrosion resistance and the stainless property of the steel can be ensured. However, the excessive Cr content promotes the formation of high-temperature ferrite and network carbide and affects the service performance of the steel, so the Cr content is controlled to be 10.0-14.0%.
Mo: molybdenum can improve the hardenability of steel in steel, and meanwhile, mo and C, N elements are combined to generate carbide and carbonitride, so that the secondary hardening capacity and tempering stability of steel are improved. Mo is also a main element for improving corrosion resistance, but the excessive content of Mo promotes ferrite formation and reduces the strength and toughness of steel.
V: vanadium can reduce the overheat sensitivity of steel, a small amount of V element can refine grains, and proper heat treatment promotes carbide to disperse and separate out, thereby playing a role in strengthening secondary hardening. However, too high a V content will increase the probability of primary carbide formation in the steel, affecting the toughness of the steel. The V content is controlled to be 0.005-1.00%.
N: nitrogen is a gap solid solution element, can produce remarkable solid solution strengthening effect, and can also improve the corrosion resistance of steel. The invention can reduce coarse carbide formed by combining excessive C content with Cr by replacing part C with N, thereby being unfavorable for the uniformity of the structure and the polishing performance. High hardness is obtained by N alloying in order to improve polishing performance. At the same time, a small amount of N is combined with Cr and V to separate out Cr with tiny dispersion distribution in the tempering process 2 N and NV carbide play a role in precipitation strengthening, so that the steel has high hardness, the polishing performance is further improved, and the wear resistance of the steel is further improved. The invention uses the nitrogen distribution strengthening concept to control the N to be 0.15% -0.50%.
P: phosphorus forms microscopic segregation when molten steel is solidified, and then is biased to grain boundaries when heated at an austenitizing temperature, so that the brittleness of the steel is remarkably increased. The invention controls the content of P below 0.030%, and the lower the content is, the better.
S: sulfur is an unavoidable impurity, forming FeS, imparting hot shortness to the steel strip. The invention controls the S content below 0.030%, and the lower the S content is, the better.
In order to further improve the comprehensive properties of the high-uniformity high-mirror-finish-property die steel, the components of the high-uniformity high-mirror-finish-property die steel may further comprise one or more of the following elements in percentage by mass: cu is less than or equal to 0.5 percent, nb is less than or equal to 0.05 percent, co is less than or equal to 0.5 percent, and rare earth element is less than or equal to 0.05 percent.
The functions and the proportions of the elements are as follows:
cu: copper is an austenite forming element, can improve corrosion resistance and can cause secondary hardening effect, but the overheat sensitivity tendency can occur when the copper content is too high, and the copper content is controlled to be less than or equal to 0.5 percent.
Nb: niobium can refine grains, increase the coarsening temperature of the grains, reduce the overheat sensitivity and the tempering brittleness of the steel, and improve the strength and the toughness of the steel under certain conditions. In the invention, less than or equal to 0.05 percent of niobium is added.
Co: cobalt is an austenite forming element, improving tempering stability. The cobalt can improve the strength performance of the steel in a solid solution strengthening mode, and can promote the dispersion precipitation strengthening effect of the second phase, so that the ultra-high strength and good comprehensive mechanical properties are obtained. The cobalt content is controlled to be less than or equal to 0.5 percent.
Rare earth element: the rare earth elements can refine the as-cast structure of the steel, and for large-specification steel, large ingot steel ingot smelting is required, and when necessary, the segregation of the as-cast structure is relieved by adding a small amount of rare earth elements, so that a uniform solidification structure is obtained. Meanwhile, the rare earth element can improve the plasticity and impact toughness of the steel, further strengthen the beneficial effects of silicon and manganese and enhance the oxidation resistance of the alloy. Rare earth elements less than or equal to 0.05% are added in the invention.
In order to further improve the overall properties of the high-uniformity high-mirror-finish property die steel, the high-uniformity high-mirror-finish property die steel may comprise, in mass percent: c:0.11 to 0.30 percent, si:0.20 to 0.80 percent of Mn:0.20 to 0.80 percent, cr:10.2 to 13.7 percent of Ni:0.2 to 1.9 percent of Mo:0.5 to 1.0 percent, V:0.005% -0.95%, N:0.15 to 0.50 percent, and the balance of Fe and unavoidable impurities.
The invention also provides a preparation method of the high-uniformity high-mirror polishing die steel, which comprises the following steps:
step 1, smelting and pouring to obtain an electrode blank, and carrying out slow cooling or heat preservation annealing treatment at 800-900 ℃ on the electrode blank;
step 2, remelting the electrode blank by a pressurizing electroslag furnace, casting into a steel ingot, and performing slow cooling or heat preservation annealing treatment at 800-900 ℃ on the steel ingot;
step 3, forging the steel ingot to obtain a forging stock;
step 4, performing dispersion treatment on the forging stock;
step 5, annealing the steel subjected to the dispersion treatment;
step 6, quenching the annealed steel, and tempering; or quenching the annealed steel, performing deep cooling treatment, and then performing tempering treatment.
Specifically, in the step 1, the smelting may be performed by using a converter, an electric furnace, an induction furnace and external refining.
Specifically, in the step 3, forging includes: and (5) forging after fully heating and preserving the heat of the steel ingot. Considering that the over-high heating temperature or the over-long heat preservation time can cause abnormal tissue of the steel ingot overburning to influence the subsequent processing and use performance of the steel, and the over-high heating temperature and the over-long heat preservation time waste energy; the heating temperature is low or the heat preservation time is short, and the homogenization effect of the tissue and carbide cannot be achieved, so that the heating temperature is controlled to be 1160-1200 ℃ and the heat preservation time is 10-15 h.
Specifically, in the step 3, considering that the excessive initial forging temperature may cause excessive burning and overheating, the too low initial forging temperature shortens the forging operation time, shortens the forging temperature range, and causes forging difficulty; the forging temperature is too high, the grains grow up rapidly at high temperature after forging, so that the grains of the forging are coarse, the mechanical property of the forging is reduced, the forging has poor plasticity, difficult deformation and increased internal stress due to the too low forging temperature, and the forging is cracked, so that the forging starting temperature is controlled to be 1160-1200 ℃, and the forging finishing temperature is controlled to be 830-860 ℃.
Specifically, in the step 4, the dispersion treatment includes: heating the forging stock to 980-1020 ℃ for heat preservation for 1-2 h, and then cooling to room temperature; then preserving heat for 2-4 hours at the temperature of 630-670 ℃ for the second time, and cooling to room temperature.
Specifically, in the step 4, the effect of the first heat preservation is to make the steel reach the austenitizing temperature, the carbide is dissolved and refined, and the structure and the crystal grains are coarsened in consideration of the fact that the first heat preservation temperature is too high and the heat preservation time is too long; the heat preservation temperature is too low and the heat preservation time is too short, so that the effect of carbide dissolution and refinement is difficult to achieve, and therefore, the first heat preservation temperature is controlled to 980-1020 ℃ and the heat preservation time is controlled to 1-2 h.
Specifically, in the step 4, the second heat preservation is performed to obtain a granular pearlite structure in which granular carbide is uniformly dispersed and distributed with ferrite as a matrix. Considering that the second heat preservation temperature is too high or too low to exceed the pearlite formation temperature range, the heat preservation time is too long to cause coarse structure and too short to achieve the effect of pearlite dispersion distribution, the second heat preservation temperature is controlled to be 630-670 ℃, and the heat preservation is carried out for 2-4 hours.
Specifically, in the above step 5, the annealing treatment has the effects of reducing the hardness of the steel, improving the machinability and the processing performance, eliminating or reducing the internal stress, preventing deformation and cracking during the processing, and refining the grains, and uniform chemical composition and structure. The annealing treatment comprises the following steps: heating the steel subjected to the dispersion treatment to 850+/-10 ℃, and preserving heat for 1-2 hours; furnace cooling to 650+/-10 ℃, preserving heat for 1-2 h, and then discharging after furnace cooling to below 400 ℃. The granular pearlite is the most ideal annealed structure state, not only can ensure the uniformity of the structure, but also has lower hardness, and is convenient for subsequent cutting processing. According to the structural transformation and phase transformation characteristics of the steel, the steel is required to be subjected to specific austenitizing at 850+/-10 ℃, and in the temperature range, a little undissolved carbide is reserved as non-spontaneous nucleation points for supercooled austenite decomposition to form pearlite crystal nuclei; then supercooled austenite decomposition is carried out in the temperature range of 650+/-10 ℃ to obtain a granular pearlite structure with ferrite as a matrix and granular carbide uniformly dispersed and distributed; the pearlite transformation is completed and stabilized after cooling to 400 ℃, and the furnace is discharged.
Specifically, in the step 6, the quenching treatment includes: preserving heat for 0.5-2 h at 950-1050 ℃, discharging, water-cooling or oil-cooling to room temperature.
Specifically, in the step 6, the cryogenic treatment is to reduce the content of retained austenite in the quenched steel, improve the strength and hardness of the steel, and the cryogenic treatment includes: preserving heat for 0.5-2 h at-73 to-84 ℃.
Specifically, in the step 6, tempering treatment may be performed at 150 to 520 ℃.
Specifically, in the above step 5, the annealed steel material has good uniformity, and the hardness difference at different positions is small, for example, the hardness difference at different positions is within 7 HB.
Specifically, in the step 5, the hardness of the annealed steel material is 185HB or less, and the machinability is excellent.
Specifically, in the step 6, the tempered steel material has a structure of martensite+fine dispersed carbide and carbonitride precipitated phases, martensite laths are uniform, no obvious network segregation and strap segregation are seen, the structure is more uniform, the sizes of the carbide and the carbonitride are less than 1 mu m, the fine dispersion is distributed on a matrix structure, and the uniformity of the structure is beneficial to the improvement of various service performances of the steel.
Specifically, in the step 6, the tempered steel material has a relatively high tempering hardness, for example, when tempered at 150 ℃, the hardness reaches above 54HRC (for example, 54.8-57.5 HRC); when tempered at 200 ℃, the hardness reaches above 55.5HRC (for example, 55.7-58.5 HRC); when tempered at 300 ℃, the hardness reaches above 53HRC (for example, 53.4-57 HRC); when tempered at 350 ℃, the hardness reaches above 53HRC (for example, 53.2-55.5 HRC); when tempered at 400 ℃, the hardness reaches above 54.5HRC (for example, 54.5-56.5 HRC); when tempered at 450 ℃, the hardness reaches more than 55HRC (for example, 55-58 HRC); when tempered at 500 ℃, the hardness reaches 56.5HRC or higher (for example, 56.5 to 60 HRC).
Specifically, in the step 6, the tempered steel material has high impact toughness, for example, quenching at 1030 ℃, the impact toughness Aku after tempering at 240 ℃ is not less than 25J (for example, 25.1 to 32J), quenching at 1030 ℃, and the impact toughness Aku after tempering at 500 ℃ is not less than 9.5J (for example, 9.6 to 12J).
Specifically, in the step 6, the roughness of the tempered steel material is low, and the polishing performance of Ra 0.01 μm level can be obtained, thereby realizing the requirements of mirror polishing performance.
Specifically, in the step 6, the tempered steel material is subjected to 120h salt spray corrosion experiment by adopting 5% NaCl solution, so that the corrosion rate and corrosion weight loss are low, and the corrosion resistance is highExcellent. For example, corrosion rate is 0.009g/m 2 H is less than or equal to 0.0095 mm/a.
Compared with the prior art, the die steel with high uniformity and high mirror polishing performance reduces carbide and tissue segregation by adopting low C and adding a proper amount of Cr, mo, V and N elements, and obtains the structure of martensite, fine dispersed carbide and carbonitride precipitated phases under the proper dispersion treatment and quenching and tempering processes, wherein martensite laths are uniform, no obvious net segregation and strip segregation are seen, so that the die steel with high uniformity and high mirror polishing performance and excellent corrosion resistance is obtained.
The die steel with high uniformity and high mirror polishing performance prepared by the components and the method has good comprehensive mechanical properties, and the annealed steel has good uniformity and excellent cutting performance. The tempered steel has uniform structure, higher tempering hardness, higher impact toughness and lower roughness, meets the requirements of mirror polishing performance, and has excellent corrosion resistance.
Examples 1 to 6
Examples 1 to 6 of the present invention provide a high-uniformity high-mirror-finish mold steel and a method for producing the same, the components of examples 1 to 4 steel comprising, in mass percent: c:0.10 to 0.30 percent, si: less than or equal to 1 percent, mn: less than or equal to 1 percent, cr:10.0 to 14.0 percent of Ni:0.2 to 2.0 percent, mo:0.5 to 1.0 percent, V:0.005% -1.00%, N:0.15 to 0.50 percent, and the balance of Fe and unavoidable impurities.
Specifically, the steel of examples 5 to 6 may further include one or more elements selected from the following elements, in mass percent: cu is less than or equal to 0.5 percent, nb is less than or equal to 0.05 percent, co is less than or equal to 0.5 percent, and rare earth element is less than or equal to 0.05 percent.
The compositions of the steels of examples 1-6 are shown in Table 1 below.
The preparation method of the steel of examples 1 to 6 includes:
(1) Casting molten steel into an ingot;
(2) Heating the cast ingot to 1160-1200 ℃, preserving heat for 10-15 hours, and forging to prepare bars with phi 130mm and phi 170 mm; the initial forging temperature is 1160-1200 ℃, and the final forging temperature is 830-860 ℃;
(3) Carrying out dispersion treatment on the bar: heating to 980-1020 ℃ for heat preservation for 1-2 h at the first heat preservation temperature, and then cooling to room temperature; then preserving heat for 2-4 hours at the second heat preservation temperature of 630-670 ℃, and air cooling to room temperature;
(4) Then annealing treatment is carried out: heating the steel subjected to the dispersion treatment to 850+/-10 ℃ for heat preservation for 1-2 hours, slowly cooling to 650+/-10 ℃ for heat preservation, and discharging the steel from the furnace at a temperature lower than 400 ℃; processing into a sample, and quenching, deep cooling and tempering. Wherein, quenching is carried out at 950-1050 ℃ and tempering is carried out at 150-520 ℃. The properties are shown in tables 2 to 7.
As can be seen from tables 2 to 7, the steels of the present invention have excellent structural uniformity, and simultaneously have good polishing properties, toughness and corrosion resistance.
Specifically, as shown in Table 2, after forging and annealing, the steels of examples 1 to 6 were subjected to annealing hardness test at three positions of the edge, quarter and center, and the annealed steels of the present invention were compared with the comparative steels, and the annealed steels of the present invention were less than or equal to 185HB in annealed hardness, and the annealed hardness difference at each position was small (the hardness difference at different positions was within 7 HB), and were excellent in machinability and had good uniformity.
Specifically, the tempered structures of the comparative steels of examples 1 to 6 were martensite+carbonitride after the same temperature quenching and different temperature tempering, fig. 1 was 50× the tempered structure of example 2, fig. 2 was 100× the tempered structure of comparative example 1, and the comparative steel had macrostructure segregation and significant large-grain carbide, and the steel of the present invention had no structure segregation, and the carbide and carbonitride precipitated phases were fine and uniformly distributed, and had a more uniform structure, as compared with the comparative steel. Fig. 3 is a drawing of 500 x in a tempered structure of the steel of example 1 after tempering at 240 ℃, and fig. 4 is a drawing of 500 x in a tempered structure of the steel of comparative example 1 after tempering at 240 ℃; fig. 5 shows a tempered structure 500× of the steel of example 1 after tempering at 500 ℃, and fig. 6 shows a tempered structure 500× of the steel of comparative example 1 after tempering at 500 ℃.
Specifically, as shown in tables 3 and 4, the steel of the present invention and the comparative example steel have higher tempering hardness at 150 ℃ or higher by quenching at the same temperature and tempering at different temperatures.
Specifically, as shown in table 5, the steel of the invention has higher impact toughness than the comparative steel through quenching at the same temperature and tempering at different temperatures, and can better meet the requirement of high toughness.
Specifically, as shown in Table 6, the steel of the present invention has lower roughness than the comparative steel by quenching at the same temperature and tempering at 240℃and surface roughness detection by a surface roughness tester, and can obtain polishing performance of Ra 0.01 μm level, thereby realizing the requirements of mirror polishing performance.
Specifically, as shown in Table 7, after quenching at the same temperature and tempering at 240 ℃, a salt spray corrosion experiment is carried out for 120 hours by adopting a 5% NaCl solution, the steel of the invention has lower corrosion rate and corrosion weight loss than the comparative steel, has more excellent corrosion resistance and can meet the requirement of corrosion resistance.
TABLE 1 chemical composition (%)
Table 2 annealing hardness of example and comparative steels
Table 3 hardness values of examples and comparative steels tempered at different temperatures after quenching at 1030 ℃ to 73 ℃ and deep cooling
Table 4 hardness values of examples and comparative steels tempered at different temperatures after quenching at 1050 ℃ to 73 ℃ and deep cooling
Table 5 impact toughness of examples and comparative steels tempered at 1030 ℃ at different temperatures
Table 6 polishing properties of examples and comparative examples quenched at 1030 ℃ to a tempering at 240 °c
Table 7 Corrosion resistance of examples and comparative steels quenched at 1030℃and tempered at 240 ℃
The present invention is not limited to the above-mentioned embodiments, and any changes or substitutions that can be easily understood by those skilled in the art within the technical scope of the present invention are intended to be included in the scope of the present invention.
Claims (10)
1. The high-uniformity high-mirror-finish-performance die steel is characterized by comprising the following components in percentage by mass: c:0.10 to 0.30 percent, si: less than or equal to 1 percent, mn: less than or equal to 1 percent, cr:10.0 to 14.0 percent of Ni:0.2 to 2.0 percent, mo:0.5 to 1.0 percent, V:0.005% -1.00%, N:0.15 to 0.50 percent, and the balance of Fe and unavoidable impurities.
2. The high-uniformity high-mirror-finish mold steel according to claim 1, wherein the components of the high-uniformity high-mirror-finish mold steel further comprise one or more selected from the following elements in mass percent: cu is less than or equal to 0.5 percent, nb is less than or equal to 0.05 percent, co is less than or equal to 0.5 percent, and rare earth element is less than or equal to 0.05 percent.
3. The high-uniformity high-mirror-finish mold steel according to claim 1, wherein the high-uniformity high-mirror-finish mold steel comprises the components in mass percent: c:0.11 to 0.30 percent, si:0.20 to 0.80 percent of Mn:0.20 to 0.80 percent, cr:10.2 to 13.7 percent of Ni:0.2 to 1.9 percent of Mo:0.5 to 1.0 percent, V:0.005% -0.95%, N:0.15 to 0.50 percent, and the balance of Fe and unavoidable impurities.
4. A method for preparing a high-uniformity high-specular finish performance die steel, characterized by being used for preparing the high-uniformity high-specular finish performance die steel according to any one of claims 1 to 3, comprising:
step 1, smelting and pouring to obtain an electrode blank, and carrying out slow cooling or heat preservation annealing treatment on the electrode blank;
step 2, remelting the electrode blank by a pressurizing electroslag furnace, casting into a steel ingot, and carrying out slow cooling or heat preservation annealing treatment on the steel ingot;
step 3, forging the steel ingot to obtain a forging stock;
step 4, performing dispersion treatment on the forging stock;
step 5, annealing the steel subjected to the dispersion treatment;
step 6, quenching the annealed steel, and tempering; or quenching the annealed steel, performing deep cooling treatment, and then performing tempering treatment.
5. The method according to claim 4, wherein in the step 3, forging includes: fully heating and preserving heat of the steel ingot, and forging; the heating temperature is controlled to 1160-1200 ℃, and the heat preservation time is 10-15 h.
6. The method according to claim 4, wherein in the step 3, the initial forging temperature is 1160 to 1200 ℃ and the final forging temperature is 830 to 860 ℃.
7. The method according to claim 4, wherein in the step 4, the dispersing treatment comprises: heating the forging stock to 980-1020 ℃ for heat preservation for 1-2 h, and then cooling to room temperature; then preserving heat for 2-4 hours at the temperature of 630-670 ℃ for the second time, and cooling to room temperature.
8. The method according to claim 4, wherein in the step 5, the annealing treatment comprises: heating the steel subjected to the dispersion treatment to 850+/-10 ℃, and preserving heat for 1-2 hours; furnace cooling to 650+/-10 ℃, preserving heat for 1-2 h, and then discharging after furnace cooling to below 400 ℃.
9. The method according to claim 4, wherein in the step 6, tempering is performed at 150 to 520 ℃.
10. The method according to any one of claims 4 to 9, wherein in step 6, the tempered steel material has a structure of martensite+fine dispersed carbide and carbonitride precipitated phases, and the martensite laths are uniform, and no significant network segregation and no band segregation are observed.
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Citations (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4504554A (en) * | 1981-04-03 | 1985-03-12 | Hitachi, Ltd. | Rotor shaft of steam turbine |
| CN1676653A (en) * | 2005-04-18 | 2005-10-05 | 宝钢集团上海五钢有限公司 | Anticorrosion, wear-resistant plastic die steel 4Cr16Mo and its mirror large-die-block preparing and producing method |
| RU2008145343A (en) * | 2008-11-17 | 2010-05-27 | Федеральное Государственное Унитарное Предприятие "Центральный Научно-Исследовательский Институт Конструкционных Материалов "Промет | MARTENSITE NITROGEN-CONTAINING CORROSION-RESISTANT STEEL |
| CN106978564A (en) * | 2017-03-30 | 2017-07-25 | 钢铁研究总院 | A kind of precipitation hardening type plastic die steel and preparation method thereof |
| CN110541124A (en) * | 2019-09-10 | 2019-12-06 | 成都先进金属材料产业技术研究院有限公司 | nitrogenous plastic die steel slab and process method thereof |
| RU2724766C1 (en) * | 2019-05-23 | 2020-06-25 | Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") | High-strength corrosion-resistant steel |
| CN111334702A (en) * | 2020-03-20 | 2020-06-26 | 浙江天马轴承集团有限公司 | Preparation method of high-strength high-nitrogen rare earth stainless bearing steel |
| CN111893381A (en) * | 2020-07-18 | 2020-11-06 | 钢铁研究总院 | High-nitrogen stainless bearing steel and preparation method thereof |
| CN113604731A (en) * | 2021-07-05 | 2021-11-05 | 昆山东大特钢制品有限公司 | High-mirror-surface corrosion-resistant plastic mold steel and production process thereof |
| CN114438416A (en) * | 2022-01-30 | 2022-05-06 | 四川六合特种金属材料股份有限公司 | Cr-Mo-V-N alloy material for bottle blank mold and preparation method thereof |
| CN114959438A (en) * | 2021-02-20 | 2022-08-30 | 天津钢研海德科技有限公司 | High-corrosion-resistance high-toughness die steel and preparation method thereof |
-
2022
- 2022-12-27 CN CN202211727530.7A patent/CN116083801A/en active Pending
Patent Citations (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4504554A (en) * | 1981-04-03 | 1985-03-12 | Hitachi, Ltd. | Rotor shaft of steam turbine |
| CN1676653A (en) * | 2005-04-18 | 2005-10-05 | 宝钢集团上海五钢有限公司 | Anticorrosion, wear-resistant plastic die steel 4Cr16Mo and its mirror large-die-block preparing and producing method |
| RU2008145343A (en) * | 2008-11-17 | 2010-05-27 | Федеральное Государственное Унитарное Предприятие "Центральный Научно-Исследовательский Институт Конструкционных Материалов "Промет | MARTENSITE NITROGEN-CONTAINING CORROSION-RESISTANT STEEL |
| CN106978564A (en) * | 2017-03-30 | 2017-07-25 | 钢铁研究总院 | A kind of precipitation hardening type plastic die steel and preparation method thereof |
| RU2724766C1 (en) * | 2019-05-23 | 2020-06-25 | Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") | High-strength corrosion-resistant steel |
| CN110541124A (en) * | 2019-09-10 | 2019-12-06 | 成都先进金属材料产业技术研究院有限公司 | nitrogenous plastic die steel slab and process method thereof |
| CN111334702A (en) * | 2020-03-20 | 2020-06-26 | 浙江天马轴承集团有限公司 | Preparation method of high-strength high-nitrogen rare earth stainless bearing steel |
| CN111893381A (en) * | 2020-07-18 | 2020-11-06 | 钢铁研究总院 | High-nitrogen stainless bearing steel and preparation method thereof |
| CN114959438A (en) * | 2021-02-20 | 2022-08-30 | 天津钢研海德科技有限公司 | High-corrosion-resistance high-toughness die steel and preparation method thereof |
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