CN111118383A - Powder steel and preparation method thereof - Google Patents
Powder steel and preparation method thereof Download PDFInfo
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- CN111118383A CN111118383A CN201911276046.5A CN201911276046A CN111118383A CN 111118383 A CN111118383 A CN 111118383A CN 201911276046 A CN201911276046 A CN 201911276046A CN 111118383 A CN111118383 A CN 111118383A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
- C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
- B22F3/15—Hot isostatic pressing
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/17—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by forging
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
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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
- C21D1/32—Soft annealing, e.g. spheroidising
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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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
- C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
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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
- C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
- B22F2003/248—Thermal after-treatment
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Abstract
The invention provides powder steel, which comprises the following components: 1.6-2.0 wt% of C; si is less than or equal to 0.60 wt%; mn is less than or equal to 0.35 wt%; 4.00-5.20 wt% of Cr; 3.50-6.50 wt% of Mo; 4.50-8.00 wt% of W; 4.00-6.00 wt% of V; 6.00-9.00 wt% of Co; p is less than or equal to 0.030 wt%; s is less than or equal to 0.030 wt%; the balance being Fe. The powder steel provided by the invention contains C, Si, Mn, Cr, Mo, W, Co, V, P and S elements, W, Mo and V are strong carbide forming elements and mainly play a role in precipitation strengthening, and Co can improve the red hardness of the steel. The powder steel provided by the invention obtains good performance under the comprehensive action of the alloy elements and the contents of the alloy elements. The invention also provides a preparation method of the powder steel.
Description
Technical Field
The invention relates to the field of steel material manufacturing, in particular to powder steel and a preparation method thereof.
Background
The die steel is used for manufacturing high-performance cutting tools, such as end mills, planing tools, screw taps, hobbing cutters and the like, and has wide application. The use of Powder Metallurgy (PM) tool steel greatly reduces the cost of a single piece from the point of view of the overall economy of the tool. Although powder tool steels are initially expensive, they can greatly extend the life of the tool, reduce down time, and also benefit the user. From a metallurgical point of view, powder metallurgy tool steels produced according to special methods have a longer life than conventional tool steels, especially high-alloyed or ultra-high alloyed steel grades. The carbide of the powder metallurgy tool steel is fine and evenly distributed, the formed carbide is granular, the smaller the size is, the more even the distribution is, the more the service life of the cutter can be prolonged. In the process of preparing the powder steel, the influence of the components of the metal powder on the performance of the powder steel is most remarkable. Therefore, how to obtain better performing powder steel becomes a hot spot for those skilled in the art to study.
Disclosure of Invention
In view of the above, the present invention provides a powder steel and a method for manufacturing the same, and the powder steel provided by the invention has good properties.
The invention provides powder steel, which comprises the following components:
1.6-2.0 wt% of C;
Si≤0.60wt％；
Mn≤0.35wt％；
4.00-5.20 wt% of Cr;
3.50-6.50 wt% of Mo;
4.50-8.00 wt% of W;
4.00-6.00 wt% of V;
6.00-9.00 wt% of Co;
P≤0.030wt％；
S≤0.030wt％；
the balance being Fe.
In the present invention, the mass content of C is preferably 1.7 to 1.9%, and more preferably 1.8%.
In the present invention, the Si content is preferably 0.1 to 0.5% by mass, more preferably 0.2 to 0.4% by mass, and most preferably 0.3% by mass.
In the present invention, the Mn content is preferably 0.1 to 0.3% by mass, and more preferably 0.2% by mass.
In the present invention, the mass content of Cr is preferably 4.5 to 5%.
In the present invention, the mass content of Mo is preferably 4 to 6%, and more preferably 5%.
In the present invention, the mass content of W is preferably 5 to 7%, and more preferably 6%.
In the present invention, the mass content of V is preferably 4.5 to 5.5%, more preferably 5%.
In the present invention, the mass content of Co is preferably 7 to 9%, and more preferably 8%.
In the present invention, W and Mo may both form M of the same type as C6C、M2C carbide, wherein M6Typical carbide of C is Fe4W2C、Fe3W3C and Fe2W4C, wherein Mo can replace W, and the hardness is 73.5 HRC-77 HRC; m2C typical carbide is W (Mo)2C; primary eutectic carbide M formed6C has high stability and melting point, can be melted only at 1150-1300 ℃, can lead the quenching temperature of steel to be close to the melting point, and because M6The C carbide has higher hardness and is not easy to accumulate and grow, and the wear resistance of the high-speed steel can be improved. In addition to this, W andmo can also form a large amount of secondary carbides, and M in martensite during the tempering process at 650-700 DEG C2The precipitation of C causes secondary hardening and increases red hardness. This is not replaceable by other alloying elements.
Co is a non-carbide-forming element, unlike other elements, and has only a very small amount of M6C exists in a carbide form; co can refine carbides and increase the red hardness, secondary hardening effect and hot hardness of high-speed steel. Co can improve the dislocation density of martensite in the tempering process and increase carbide nucleation sites; co increases the activity of C in Fe, so that carbide is more easily precipitated, the concentration gradient of C is reduced, the diffusion flow of C is reduced, and the accumulation speed of the carbide is slowed down to prevent the carbide from being coarse.
The powder steel provided by the invention contains C, Si, Mn, Cr, Mo, W, Co, V, P and S elements, wherein the alloy elements playing a main strengthening role are W, Mo, Co and V. W, Mo and V are strong carbide forming elements and mainly play a role in precipitation strengthening, and Co can improve the red hardness of the steel; the tempered microstructure of the powder steel provided by the invention is martensite + carbide. The powder steel provided by the invention obtains good performance under the comprehensive action of the alloy elements and the contents of the alloy elements.
The invention provides a preparation method of powder steel, which comprises the following steps:
carrying out hot isostatic pressing on the alloy powder, and then cooling to obtain a pressed part;
and sequentially heating, forging, annealing, quenching and tempering the pressed part to obtain the powder steel.
In the invention, the alloy powder comprises the alloy powder of the component elements of the powdered steel in the technical scheme, namely C powder, Si powder, Mn powder, Cr powder, Mo powder, W powder, V powder, Co powder and Fe powder. In the invention, the particle size of the alloy powder is preferably 0-150 microns, more preferably 10-120 microns, more preferably 50-100 microns, and most preferably 60-80 microns. In the present invention, the particle size of the powder of each element in the alloy powder and the particle size of the alloy powder obtained by mixing the powder of each element are preferably both within the above particle size range.
In the invention, the temperature of hot isostatic pressing is preferably 1100-1200 ℃, more preferably 1120-1180 ℃, most preferably 1140-1160 ℃, and most preferably 1130 ℃; the pressure of the hot isostatic pressing is preferably 100-150 MPa, more preferably 110-140 MPa, and most preferably 120-130 MPa; the heat preservation time of the hot isostatic pressing is preferably 2-4 hours, and more preferably 3 hours.
In the present invention, the hot isostatic pressing process results in a more uniform and fine microstructure; the matching of the hot isostatic pressing temperature and the pressure plays an important role in the microstructure of a sample, the microstructure needs to be uniform and compact to the maximum extent to obtain a product with excellent performance, and the tissue defect is reduced to the minimum. If the temperature is lower and the pressure is lower, the bonding degree of the alloy powder is reduced, a large number of structural defects can be caused, and the mechanical performance is seriously influenced; if the temperature is higher and the pressure is higher, the microstructure grows too much, the mechanical property of the coarsened microstructure is poorer, and the requirement of the performance cannot be met. The present invention preferably enables to obtain powder steel with good properties within the above mentioned hot isostatic pressing process parameters.
In the present invention, the cooling method is preferably:
and cooling the hot isostatic pressed product to 800-900 ℃, preserving heat, and then slowly cooling to room temperature.
In the invention, the cooling rate is preferably 0.005-0.05 ℃/s, more preferably 0.01-0.04 ℃/s, more preferably 0.02-0.03 ℃/s; the cooling temperature is preferably 820-880 ℃, and more preferably 840-860 ℃.
In the present invention, the heat-insulating time is preferably 2 to 4 hours, and more preferably 3 hours.
In the present invention, the cooling rate of the slow cooling is preferably 0.005 to 0.015 ℃/s, more preferably 0.008 to 0.012 ℃/s, and most preferably 0.01 ℃/s.
By adopting the cooling method, the effects of softening and annealing can be achieved by firstly cooling to 800-900 ℃ for heat preservation and then slowly cooling to room temperature, so that the stress is reduced, and the cracking is prevented.
In the invention, the heating temperature is preferably 1150-1170 ℃, more preferably 1155-1165 ℃, and most preferably 1160 ℃. In the invention, after heating, the heated product is preferably subjected to heat preservation and then forging; the heat preservation time is preferably 0.5-1.5 hours, and more preferably 1 hour.
In the invention, the forging temperature is preferably 1000-1200 ℃, more preferably 1050-1150 ℃, and most preferably 1100 ℃; the final forging temperature of the forging is preferably above 900 ℃, more preferably 900-950 ℃, and most preferably 920-930 ℃.
In the present invention, the annealing method is preferably:
and heating the forged product to 750-800 ℃, preserving heat for 2-6 hours for primary annealing, then slowly cooling to 650-740 ℃, preserving heat for 6-10 hours, and carrying out secondary annealing.
In the invention, the heating temperature of the primary annealing is preferably 760-780 ℃, and the heat preservation time is preferably 6 hours; the slow cooling temperature of the secondary annealing is preferably 680-720 ℃, more preferably 700 ℃, and the heat preservation time is preferably 8 hours. In the present invention, the cooling speed of the slow cooling is the same as that of the above technical solution, and is not described herein again.
The annealing method is preferably adopted for annealing, the two-stage heat preservation annealing is isothermal spheroidizing annealing, uniform spheroidized annealed tissues can be obtained, and compared with the conventional one-stage heat preservation annealing process, the annealing time is shortened, the cost is reduced, the production efficiency is improved, and the obtained powder steel has better performance.
In the present invention, the quenching method is preferably:
and heating the annealed product to 1000-1250 ℃, preserving heat for 30 minutes, and carrying out oil medium (or vacuum gas quenching) quenching.
In the invention, the heating temperature in the quenching process is preferably 1050-1200 ℃, and more preferably 1100-1150 ℃.
The invention preferably adopts the quenching medium, reduces the risk of quenching cracking compared with water quenching, improves the quenching cooling speed compared with air quenching, is favorable for forming a quenched martensite structure, and further ensures that the powder steel prepared by the invention has better performance.
In the present invention, the tempering method is preferably:
and heating the quenched product to 530-650 ℃, preserving the heat for 1 hour, and cooling the product to room temperature in air.
In the present invention, the tempering is preferably performed two to three times, that is, the tempering is performed two to three times after performing the first tempering according to the above-mentioned tempering method and then repeating the operation one to two times.
In the invention, the tempering temperature is preferably 550-620 ℃, more preferably 500-580 ℃, and most preferably 550 ℃.
The components of the powder steel and the preparation method suitable for the components enable the prepared powder steel to have uniform and fine microstructure, overcome the formation of various structural defects in the prior art, obtain a precipitated phase with fine size and grain size, and enable the powder steel to have excellent comprehensive performance, remarkably prolonged service life, excellent performance and strong economical efficiency.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all embodiments. All other examples, which may be modified or appreciated by those of ordinary skill in the art based on the examples given herein, are intended to be within the scope of the present invention.
Example 1
Mixing C powder, Si powder, Mn powder, Cr powder, Mo powder, W powder, V powder, Co powder and Fe powder to obtain alloy powder;
hot isostatic pressing is carried out on the alloy powder, the temperature is 1130 ℃, the pressure is 120MPa, and the heat preservation is carried out for 3 hours; then cooling to 760 ℃ at the speed of 0.02 ℃/s, preserving the heat for 4 hours, and slowly cooling to room temperature;
heating the cooled product to 1150 ℃, preserving heat for 1 hour, and then forging, wherein the forging temperature is 1100 ℃, and the finish forging temperature is 920 ℃;
heating the forged product to 780 ℃, preserving heat for 4 hours, slowly cooling to 740 ℃, preserving heat for 6 hours, slowly cooling to room temperature, and annealing;
heating the annealed product to 1150 ℃, preserving heat for 1 hour, and quenching in an oil medium;
heating the quenched product to 620 ℃, preserving heat for 2 hours, air-cooling to room temperature for tempering, repeating the tempering operation once again, and tempering twice to obtain the powder steel.
The powdered steel prepared in the example 1 of the invention is subjected to component detection by a standard method of GB/T4336-2016 spark discharge atomic emission spectrometry for measuring the contents of multiple elements in carbon steel and medium and low alloy steel, and the detection results are shown in Table 1.
The powder steel prepared in the embodiment 1 of the invention is subjected to bending strength detection by adopting a standard method of YB/T5349-.
Impact toughness of the powder steel prepared in example 1 of the present invention was measured by a standard method of GB/T22-2007 "metallic material charpy pendulum impact test method", and the measurement results are shown in table 3.
TABLE 1 chemical composition in wt% of steel prepared in inventive and comparative examples
| Steel grade | C | Si | Mn | Cr | Mo | V | W | Co | S、P | Fe |
| Example 1 | 1.89 | 0.53 | 0.29 | 4.65 | 4.96 | 4.74 | 5.89 | 8.11 | ≤0.03 | Balance of |
| Example 2 | 1.73 | 0.42 | 0.33 | 4.91 | 4.78 | 5.13 | 6.11 | 7.87 | ≤0.03 | Balance of |
| Comparative example 1 | 0.9 | 0.52 | 0.34 | 4.78 | 2.01 | 1.87 | 5.97 | - | ≤0.03 | Balance of |
Example 2
Mixing C powder, Si powder, Mn powder, Cr powder, Mo powder, W powder, V powder, Co powder and Fe powder to obtain alloy powder;
hot isostatic pressing is carried out on the alloy powder, the temperature is 1150 ℃, the pressure is 130MPa, the heat preservation is carried out for 3 hours, then the alloy powder is cooled to 760 ℃ at the speed of 0.015 ℃/s, the heat preservation is carried out for 4 hours, and the alloy powder is slowly cooled to the room temperature;
heating the cooled product to 1150 ℃, preserving heat for 1 hour, and forging, wherein the forging temperature is 1100 ℃, and the finish forging temperature is 940 ℃;
heating the forged product to 860 ℃, preserving heat for 4 hours, slowly cooling to 740 ℃, preserving heat for 6 hours, slowly cooling to room temperature for annealing;
heating the annealed product to 1180 ℃, preserving heat for 1 hour, and quenching in an oil medium;
heating the quenched product to 600 ℃, preserving heat for 2 hours, air-cooling to room temperature for tempering, repeating the tempering operation once again, and tempering twice to obtain the powder steel.
The powdered steel prepared in example 2 of the present invention was subjected to the composition test according to the method of example 1, and the test results are shown in table 1; the powder steels prepared in example 2 of the present invention were tested for their properties according to the method of example 1, and the results are shown in tables 2 and 3.
TABLE 2 flexural Strength test results of steels prepared in inventive and comparative examples
Comparative example 1
Smelting alloy raw materials by adopting a traditional intermediate frequency furnace, LF + VD + forging process to obtain an ingot;
forging, quenching and tempering the cast ingot to obtain a steel product, wherein the initial forging temperature of the forging is 1100 ℃, and the final forging temperature is 900 ℃; the quenching temperature is 1150 ℃; the tempering temperature was 600 ℃.
The steel material prepared in comparative example 1 of the present invention was subjected to component detection by the method of example 1, and the detection results are shown in table 1; the steel materials prepared in comparative example 1 of the present invention were tested for properties according to the method of example 1, and the results are shown in tables 2 and 3.
TABLE 3 impact work test results of steels prepared in examples of the present invention and comparative examples
From the above examples, the present invention provides a powder steel comprising the following components: 1.6-2.0 wt% of C; si is less than or equal to 0.60 wt%; mn is less than or equal to 0.35 wt%; 4.00-5.20 wt% of Cr; 3.50-6.50 wt% of Mo; 4.50-8.00 wt% of W; 4.00-6.00 wt% of V; 6.00-9.00 wt% of Co; p is less than or equal to 0.030 wt%; s is less than or equal to 0.030 wt%; the balance being Fe. The powder steel provided by the invention contains C, Si, Mn, Cr, Mo, W, Co, V, P and S elements, W, Mo and V are strong carbide forming elements and mainly play a role in precipitation strengthening, and Co can improve the red hardness of the steel. The powder steel provided by the invention obtains good performance under the comprehensive action of the alloy elements and the contents of the alloy elements.
While only the preferred embodiments of the present invention have been shown and described, it will be understood by those skilled in the art that various changes in form and details may be made therein without departing from the spirit and scope of the invention.
Claims (10)
1. A powder steel comprising the following components:
1.6-2.0 wt% of C;
Si≤0.60wt％；
Mn≤0.35wt％；
4.00-5.20 wt% of Cr;
3.50-6.50 wt% of Mo;
4.50-8.00 wt% of W;
4.00-6.00 wt% of V;
6.00-9.00 wt% of Co;
P≤0.030wt％；
S≤0.030wt％；
the balance being Fe.
2. A method of producing the powder steel of claim 1, comprising:
carrying out hot isostatic pressing on the alloy powder, and then cooling to obtain a pressed part;
and sequentially heating, forging, annealing, quenching and tempering the pressed part to obtain the powder steel.
3. The method of claim 2, wherein the hot isostatic pressing is performed at a temperature of 1100 to 1200 ℃, at a pressure of 100 to 150MPa, and for a holding time of 2 to 4 hours.
4. The method of claim 2, wherein the cooling is by:
and cooling the hot isostatic pressed product to 800-900 ℃, preserving heat, and then slowly cooling to room temperature.
5. The method of claim 4, wherein the cooling is at a rate of 0.005-0.05 ℃/s.
6. The method of claim 2, wherein the heating is performed at a temperature of 1150-1170 ℃.
7. The method according to claim 2, wherein the forging temperature is 1000 to 1200 ℃ and the finish forging temperature is 900 ℃ or higher.
8. The method of claim 2, wherein the annealing is performed by:
and heating the forged product to 750-800 ℃, preserving heat for 2-6 hours, carrying out primary annealing, cooling to 650-740 ℃, preserving heat for 6-10 hours, and carrying out secondary annealing.
9. The method of claim 2, wherein the quenching is performed by:
and heating the annealed product to 1000-1250 ℃, preserving heat for 30 minutes, and carrying out oil medium or vacuum gas quenching.
10. The method of claim 2, wherein the tempering is by:
and heating the quenched product to 530-650 ℃, preserving the heat for 1 hour, and cooling the product to room temperature in air.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113699460A (en) * | 2021-08-13 | 2021-11-26 | 浙江中模材料科技有限公司 | High-hardness powder steel and heat treatment method thereof |
| CN114833342A (en) * | 2022-05-12 | 2022-08-02 | 珠海市龙圣模具材料有限公司 | Powder metallurgy wear-resistant high-toughness die steel and processing technology thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61159557A (en) * | 1984-12-29 | 1986-07-19 | Daido Steel Co Ltd | Powdery high-speed steel |
| CN107604257A (en) * | 2016-08-25 | 2018-01-19 | 机械科学研究总院先进制造技术研究中心 | A kind of HM3 powder steels and its preparation technology |
-
2019
- 2019-12-12 CN CN201911276046.5A patent/CN111118383A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61159557A (en) * | 1984-12-29 | 1986-07-19 | Daido Steel Co Ltd | Powdery high-speed steel |
| CN107604257A (en) * | 2016-08-25 | 2018-01-19 | 机械科学研究总院先进制造技术研究中心 | A kind of HM3 powder steels and its preparation technology |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113699460A (en) * | 2021-08-13 | 2021-11-26 | 浙江中模材料科技有限公司 | High-hardness powder steel and heat treatment method thereof |
| CN114833342A (en) * | 2022-05-12 | 2022-08-02 | 珠海市龙圣模具材料有限公司 | Powder metallurgy wear-resistant high-toughness die steel and processing technology thereof |
| CN114833342B (en) * | 2022-05-12 | 2023-01-17 | 珠海市龙圣模具材料有限公司 | Powder metallurgy wear-resistant high-toughness die steel and processing technology thereof |
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