CN110983186A - High alloy tool steel, method for manufacturing same, and method for using same as cutting edge steel insert-joint slicing knife - Google Patents
High alloy tool steel, method for manufacturing same, and method for using same as cutting edge steel insert-joint slicing knife Download PDFInfo
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- CN110983186A CN110983186A CN201911336779.3A CN201911336779A CN110983186A CN 110983186 A CN110983186 A CN 110983186A CN 201911336779 A CN201911336779 A CN 201911336779A CN 110983186 A CN110983186 A CN 110983186A
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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
- 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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- 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
- C21D9/22—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for drills; for milling cutters; for machine cutting tools
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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
- C22C38/04—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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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Abstract
The invention discloses high-alloy tool steel which is prepared by mixing, by mass, 0.54-0.62% of C, 0.40-0.60% of Si, 0.25-0.50% of Mn, 3.80-4.40% of Cr, 2.20-2.80% of W, 6.00-6.80% of Mo, 0.70-0.90% of V, 0.15-0.25% of Ni, less than or equal to 0.03% of S and P, and the balance Fe, remelting by adding electroslag in an induction furnace or vacuum refining in an electric arc furnace, and then forging and rolling at 870-1150 ℃; when the high alloy tool steel is used as the cutting edge steel splicing planing cutter, the high alloy tool steel is placed on the position of the low carbon steel plate splicing cutting edge, and the high alloy tool steel and the low carbon steel plate are subjected to non-oxidation welding, rolling and splicing, and then are subjected to annealing, quenching and tempering in sequence to obtain the planing cutter. The high-alloy tool steel has good high-temperature plasticity, is easy to implement and control a planing cutter high-temperature non-oxidation rolling splicing process, has the tempering secondary hardening hardness after quenching reaching the hardness of the general high-speed steel, has a sharp and wear-resistant blade, and has the cutting life reaching or being longer than the service life of a general high-speed steel blade steel planing cutter.
Description
Technical Field
The invention relates to a manufacturing method and application of tool steel, in particular to high-alloy tool steel, a manufacturing method and a method for using the tool steel as a cutting edge steel splicing planing cutter.
Background
The existing planing cutter is usually manufactured by splicing universal high-speed steel serving as blade steel, although the hardness of the universal high-speed steel can meet the requirements of sharpness and wear resistance of a blade edge, the process implementation difficulty of splicing the universal high-speed steel with a blade steel body is high, the combination property of the universal high-speed steel and the blade steel body is poor, the rejection rate is high, and the production cost is high.
Disclosure of Invention
The purpose of the invention is as follows: in view of the above problems, an object of the present invention is to provide a high alloy tool steel and a method for manufacturing the same, which is suitable for use as a blade steel cutting insert, and a method for manufacturing the same.
The technical scheme is as follows: the high-alloy tool steel is prepared from the following raw materials in percentage by mass: 0.54-0.62% of C, 0.40-0.60% of Si, 0.25-0.50% of Mn, 3.80-4.40% of Cr, 2.20-2.80% of W, 6.00-6.80% of Mo6, 0.70-0.90% of V, 0.15-0.25% of Ni, less than or equal to 0.03% of S and P, and the balance of Fe.
Preferably, the high alloy tool steel is prepared from the following raw materials in percentage by mass: 0.6% of C, 0.58% of Si, 0.32% of Mn, 3.90% of Cr, 2.29% of W, 6.34% of Mo, 0.78% of V, 0.21% of Ni, 0.01% of S, 0.02% of P and the balance of Fe.
The manufacturing method of the high-alloy tool steel comprises the steps of preparing raw materials according to the proportion, remelting by adding electroslag in an induction furnace or refining in an electric arc furnace in vacuum, and then forging and rolling at 870-1150 ℃ to obtain the high-alloy tool steel.
The method for using the high-alloy tool steel as the knife edge steel splicing planing cutter comprises the steps of blanking a high-alloy tool and a low-carbon steel plate according to the size of the planing cutter, placing the high-alloy tool steel on the position of the low-carbon steel plate where the knife edge is spliced, splicing the high-alloy tool steel and the low-carbon steel plate through non-oxidation welding and rolling, and then sequentially annealing, quenching and tempering to obtain the planing cutter.
The specific process of the rolling and splicing comprises the following steps: heating at 1050-1220 deg.C, holding for 25-50 min, rolling at 1050 deg.C or lower, and over-heating at 1280 deg.C or lower.
The specific processes of annealing, quenching and tempering are as follows:
annealing, heating at 860-880 ℃, preserving heat for 4-6 hours, and then cooling along with the furnace;
quenching, heating at 1180-1220 ℃, and performing oil cooling or air cooling or water cooling after heat preservation for 0.5-1.2 min/mm;
and (4) tempering, heating at the temperature of 520-560 ℃, and keeping the temperature for 2-4 hours.
Further, the rolling reduction is not less than 35%.
Further, the number of tempering times was 3.
Has the advantages that: compared with the prior art, the invention has the advantages that: (1) the high-alloy tool steel has the advantages that the total amount of Cr, W, Mo and V alloys and the content of C are greatly lower than those of general high-speed steel, the high-alloy tool steel has good high-temperature plasticity, when the high-alloy tool steel is used as a cutting edge steel splicing planing cutter, the cutting edge steel and a low-carbon steel plate used as a cutter body belong to metallurgical bonding, the high-alloy tool steel has good bonding performance, the implementation and control of a high-temperature non-oxidation rolling splicing process are easy, and the qualification rate of semi-finished products in the splicing process is improved; (2) according to the high-alloy tool steel, through reasonable content collocation of Cr, W, Mo and V, when the content of C is in the middle, the secondary hardening hardness of tempering after the inlaying slicing knife is quenched reaches the general high-speed steel hardness, namely HRC 63-65; (3) when the planing cutter is spliced, the high-alloy tool steel contains proper quantity of quenching undissolved carbide and a small amount of Ni bonding effect, so that the cutting edge of the thin-blade cutter is sharp and wear-resistant, the cutting surface is smoother, and the cutting life reaches or is longer than that of a universal high-speed steel blade steel planing cutter; (4) the planing cutter can reduce the cost of the steel material of the cutting edge by 20 percent and reduce the total production cost of the planing cutter by 10 percent.
Drawings
FIG. 1 is a metallographic picture of a high alloy tool steel made according to the present invention;
FIG. 2 is a schematic view of the position of a high alloy tool steel as a cutting edge steel cutting edge;
FIG. 3 is a gold phase diagram at the spliced bonding surface.
Detailed Description
The invention will be further elucidated with reference to the drawings and specific examples, which are intended to illustrate the invention and are not intended to limit the scope of the invention.
The high-alloy tool steel is prepared from the following raw materials in percentage by mass: 0.54-0.62% of C, 0.40-0.60% of Si, 0.25-0.50% of Mn, 3.80-4.40% of Cr, 2.20-2.80% of W, 6.00-6.80% of Mo, 0.70-0.90% of V, 0.15-0.25% of Ni, less than or equal to 0.03% of S and P, and the balance of Fe.
Wherein, the best scheme is as follows: 0.6% of C, 0.58% of Si, 0.32% of Mn, 3.90% of Cr, 2.29% of W, 6.34% of Mo6.34%, 0.78% of V, 0.21% of Ni, 0.01% of S, 0.02% of P and the balance of Fe.
The manufacturing method of the high alloy tool steel specifically comprises the following steps: and (3) carrying out electroslag remelting on the raw materials prepared according to the proportion by adopting an induction furnace or vacuum refining in an electric arc furnace, and then forging and rolling at 870-1150 ℃ to prepare the high-alloy tool steel.
FIG. 1 is a gold phase diagram of the high alloy tool steel with the best scheme, wherein the magnification is 500 times, the microstructure particles are fine and uniform, and the austenite grain size is still very fine.
The method for using the high alloy tool steel as the cutting edge steel splicing planing cutter comprises the following specific steps:
step one, as shown in the attached figure 2, blanking a low-carbon steel plate (the carbon content is generally less than 0.25%) according to the size of a slicing knife to obtain a knife main body, wherein the knife main body comprises a knife body steel 1 part and an auxiliary steel 3 part which are integrated, blanking high-alloy tool steel to obtain a knife edge steel 2 part, and then leveling, machining, grinding a surface and milling an edge to finish primary machining.
And step two, as shown in the attached figure 2, the blade steel 2 is placed at the position of the blade body for cutting the blade, and the auxiliary steel 3 part is arranged behind the position for cutting the blade.
And step three, welding the two into a whole through non-oxidation welding at the high temperature of 1000-1200 ℃, and then rolling and splicing. The specific process of the rolling and splicing comprises the following steps: heating at 1050-1220 ℃, preserving heat for 25-50 minutes, then rolling at a temperature lower than 1050 ℃, wherein the rolling reduction rate is not lower than 35%, and then overheating and overburning at a temperature not lower than 1280 ℃.
And step four, annealing, quenching and tempering are sequentially carried out, so that the planing cutter is manufactured. The specific process of annealing, quenching and tempering comprises the following steps:
annealing, heating at 860-880 ℃, preserving heat for 4-6 hours, and then cooling along with the furnace; the hardness and texture criteria after annealing were: HB is 250-295, the average size of carbides is smaller than 1.5 mu m, and massive carbides are more;
quenching, heating at 1180-1220 ℃, and performing oil cooling or air cooling or water cooling after heat preservation for 0.5-1.2 min/mm; the hardness and texture standards after quenching were: HRC 62-64, grain size 9-10.5 grade, undissolved carbide size 0.5-1.5 μm;
tempering, heating at 520-560 ℃, and keeping the temperature for 2-4 hours, wherein the tempering times are 3 times; the hardness and texture criteria after tempering were: HRC 63-65, tempered martensite, uniformly refined carbide and residual austenite less than or equal to 12%.
By the above-mentioned bonding method, fig. 3 is a metallographic view at a magnification of 100 times in the region of the bonding surface i in fig. 2. The joint surface A is a splicing joint surface of the cutter steel 2 part and the cutter body steel 1 part, the joint surface B is a splicing joint surface of the cutter body steel 1 part and the auxiliary steel 3 part, and the joint surface C is a splicing joint surface of the auxiliary steel 3 part and the cutter steel 2 part. Therefore, the austenite grain size is fine, and the tissue grains are fine and uniform.
The high alloy tool steel as the cutting edge steel splicing planing cutter is provided with the following raw material components and content design on the basis of correlation of alloy phase equilibrium thermodynamic structure calculation, quenching tempering hardness and heat treatment temperature calculation and alloy interatomic binding energy calculation and performance:
1. the high-temperature plasticity is low when the content of C is higher than the upper limit, and the hardness is reduced when the content of C is lower than the lower limit; the brittleness is increased and the surface decarburization is increased when the Si content is higher than the upper limit, and the strength is decreased when the Si content is lower than the lower limit; the brittleness is increased when the Mn content is higher than the upper limit, and the strength is reduced when the Mn content is lower than the lower limit; when the Cr content is higher than the upper limit, the retained austenite amount is increased, the tempering temperature is deviated from the highest hardness point, and when the Cr content is lower than the lower limit, the quenching hardness is reduced; when the W content is higher than the upper limit, the high-temperature plasticity is reduced, and when the W content is lower than the lower limit, the tempering hardness is reduced; when the Mo content is higher than the upper limit, the high-temperature plasticity is low, and when the Mo content is lower than the lower limit, the tempering hardness is obviously reduced; when the V content is higher than the upper limit, blocky carbides are easy to appear, and when the V content is lower than the lower limit, the tempering hardness is reduced; when the Ni content is higher than the upper limit, the annealing and spheroidizing are difficult, and when the Ni content is lower than the lower limit, the strength is reduced;
2. below or above the annealing temperature, the annealing structure is poor or the annealing hardness is high; as can be seen from table 1, when the quenching temperature exceeds the upper limit, the crystal grains become coarse and the residual austenite is too high, which results in a decrease in hardness; as can be seen from Table 1, the tempering temperature is lowered above the upper limit of hardness and is too high below the lower limit of retained austenite.
TABLE 1 hardness values for quenching and tempering of high alloy tool steels
Compared with the prior universal high-speed steel (the carbon content is generally 0.70-1.65%) as the cutting edge steel splicing planing cutter, the high-alloy tool steel of the invention, which is used as the cutting edge steel splicing planing cutter, has the advantages that: (1) the high-alloy tool steel has the advantages that the total amount of Cr, W, Mo and V alloys and the content of C are greatly lower than those of general high-speed steel, the high-alloy tool steel has good high-temperature plasticity, when the high-alloy tool steel is used as a cutting edge steel splicing planing cutter, the cutting edge steel and a low-carbon steel plate used as a cutter body belong to metallurgical bonding, the high-alloy tool steel has good bonding property, the implementation and control of a high-temperature non-oxidation rolling splicing process are easy, and the qualification rate of semi-finished products in the splicing process is improved; (2) according to the high-alloy tool steel, through reasonable content collocation of Cr, W, Mo and V, when the content of C is limited in the application, the secondary hardening hardness of tempering after the inlaying slicing knife is quenched reaches the hardness of general high-speed steel, namely HRC 63-65; (3) when the planing cutter is spliced, the high-alloy tool steel contains proper quantity of quenching undissolved carbide and a small amount of Ni bonding effect, so that the cutting edge of the thin-blade cutter is sharp and wear-resistant, the cutting surface is smoother, and the cutting life reaches or is longer than that of a universal high-speed steel blade steel planing cutter; (4) the planing cutter can reduce the cost of the steel material of the cutting edge by 20 percent and reduce the total production cost of the planing cutter by 10 percent.
The planing cutter of the invention can be used for planing and cutting various high-grade wood veneers, and has wide application prospect in industries such as wood decorating plates and the like.
Claims (8)
1. A high alloy tool steel characterized by: the composition is prepared from the following raw materials in percentage by mass: 0.54-0.62% of C, 0.40-0.60% of Si, 0.25-0.50% of Mn, 3.80-4.40% of Cr, 2.20-2.80% of W, 6.00-6.80% of Mo6, 0.70-0.90% of V, 0.15-0.25% of Ni, less than or equal to 0.03% of S and P, and the balance of Fe.
2. The high alloy tool steel according to claim 1, wherein: the composition is prepared from the following raw materials in percentage by mass: 0.6% of C, 0.58% of Si, 0.32% of Mn, 3.90% of Cr, 2.29% of W, 6.34% of Mo, 0.78% of V, 0.21% of Ni0.01% of S, 0.02% of P and the balance of Fe.
3. A method of manufacturing the high alloy tool steel of claim 1, characterized in that: preparing raw materials according to the proportion, remelting by adopting an induction furnace and electroslag or vacuum refining by adopting an electric arc furnace, and forging and rolling at 870-1150 ℃ to prepare the high-alloy tool steel.
4. A method of using the high alloy tool steel of claim 1 as a cutting steel cutting insert, characterized in that: blanking a high alloy tool and a low carbon steel plate according to the size of the planing cutter, placing the high alloy tool steel on the position of the splicing cutting edge of the low carbon steel plate, splicing the high alloy tool steel and the low carbon steel plate through non-oxidation welding and rolling, and then sequentially annealing, quenching and tempering to obtain the planing cutter.
5. The method of cutting a veneer according to claim 4, wherein: the specific process of the rolling and splicing comprises the following steps: heating at 1050-1220 deg.C, holding for 25-50 min, rolling at 1050 deg.C or lower, and over-heating at 1280 deg.C or lower.
6. The method of cutting a veneer according to claim 4, wherein: the specific process of annealing, quenching and tempering comprises the following steps:
annealing, heating at 860-880 ℃, preserving heat for 4-6 hours, and then cooling along with the furnace;
quenching, heating at 1180-1220 ℃, and performing oil cooling or air cooling or water cooling after heat preservation for 0.5-1.2 min/mm;
and (4) tempering, heating at the temperature of 520-560 ℃, and keeping the temperature for 2-4 hours.
7. The method of cutting a veneer according to claim 4, wherein: the rolling reduction rate is not lower than 35%.
8. The method of cutting a veneer according to claim 4, wherein: the number of tempering times was 3.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114055086A (en) * | 2021-11-18 | 2022-02-18 | 辽宁忠旺集团有限公司 | 7CrSiMnMoV steel net pulling blade and manufacturing method thereof |
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