CN114318133A - Wear-resistant tool steel - Google Patents
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Abstract
The invention provides wear-resistant tool steel which is prepared by adopting a rapid solidification process, and comprises the following chemical components in percentage by mass: c: 1.5% -3.9%, Si: 0.4% -1.2%, Mn: 0.3% -1.0%, Cr: 4% -7%, Mo: 1.0% -3%, V: less than or equal to 15 percent, Ti: 0.5 to 6 percent, and the balance of Fe and impurities. The wear-resistant tool steel has the advantages of small size and uniform distribution of the second phase, excellent comprehensive mechanical property, and particularly excellent wear resistance due to the existence of the high-hardness second phase in the structure.
Description
Technical Field
The invention relates to the technical field of tool steel materials, in particular to wear-resistant tool steel.
Background
Tool steels, in particular cold work tool steels, have very high requirements with regard to their wear resistance and toughness, such as punching, stamping, bending and deep drawing, metal powder pressing, cold rolling rolls, etc. In terms of the working conditions of the application, in order to improve the service life, higher and higher requirements are put on the wear resistance of the tool steel.
The prior art proposals, mainly aiming at promoting the formation of a large amount of carbides in the tool steel to improve the wear resistance, such as M6C, M23C6, M7C3, MC and the like, wherein MC carbides mainly comprise V-rich or Nb-rich. MC carbides are commonly used in tool steels because they have a higher hardness than other types of carbides and can better prevent surface wear during tool steel application. For example, a typical commercial 10V tool steel V alloy with a mass fraction of 9.75%, the production of high V tool steel requires attention, and V and C have strong chemical bonding ability, so that they start to form and grow at the early stage of cooling solidification of molten steel, and easily cause segregation and coarse carbides, thereby affecting other necessary properties required for the tool steel, such as toughness, machinability, etc.
The V content in the powder metallurgy tool steel alloy can be designed to be very high, for example, the alloy elements in the structure can still be uniformly distributed when the 10V tool is prepared by adopting the powder metallurgy process. It is also obvious that the cost is increased along with the increase of the use amount of the V alloy element in the tool steel, and how to improve the wear resistance of the alloy on one hand and improve the cost performance of the alloy is a problem to be considered.
Disclosure of Invention
In view of the above, the present invention is directed to a wear-resistant tool steel having excellent wear resistance.
In order to achieve the purpose, the technical scheme of the invention is realized as follows:
the wear-resistant tool steel is prepared by adopting a rapid solidification process, and comprises the following chemical components in percentage by mass: c: 1.5% -3.9%, Si: 0.4% -1.2%, Mn: 0.3% -1.0%, Cr: 4% -7%, Mo: 1.0% -3%, V: less than or equal to 15 percent, Ti: 0.5 to 6 percent, and the balance of Fe and impurities.
Further, the chemical components comprise the following components in percentage by mass: c: 1.5% -3.5%, Si: 0.4% -1.2%, Mn: 0.3% -0.8%, Cr: 4% -7%, Mo: 1.0% -3%, V: less than or equal to 15 percent, Ti: 0.5 to 3 percent.
Further, the (V + Ti) range is: 5 to 16 percent.
Further, the impurities include O, and O: less than or equal to 0.03 percent.
Further, the impurities include S, and S: less than or equal to 0.3 percent.
Further, the impurities include P, and P: less than or equal to 0.05 percent.
Further, the rapid solidification process includes a powder metallurgy process or a spray forming process.
Further, the volume fraction of the Ti-rich MX carbides in the wear-resistant tool steel is 1-15%.
Furthermore, the grain size of the Ti-rich MX carbide is less than or equal to 7 μm.
Furthermore, at least 80% of the Ti-rich MX carbides have a particle size of less than or equal to 3 μm.
In the invention, specific chemical components and proportion are necessary conditions for realizing the wear resistance of the wear-resistant alloy, and the action and the principle of each chemical component are briefly described as follows:
part of the C element is dissolved in the matrix in a solid mode, so that certain hardness can be obtained after heat treatment, in addition, the C element participates in the formation of various carbides, for the wear-resistant tool steel of the embodiment, the key point for obtaining the wear resistance is to form the ultra-high hardness Ti-rich type MX carbide, wherein M represents an element mainly comprising Ti, X represents an element mainly comprising C, and the C, N mixed type MX carbide can also be formed together with N.
It should be noted that N is not an essential element for the wear-resistant tool steel of the present invention, but for cost reasons, when nitrogen is used as the atomizing medium in the gas atomization milling process, the content of N increases to a certain value, and within a certain content range, N can play a beneficial role, mainly participating in carbide formation together with C, and at this time, the content of C needs to be re-determined to maintain a proper carbon balance coefficient. The presence of too high N is considered disadvantageous for the alloy steel of the present invention, mainly due to: the increase of excessive N can lead to the atomizing process to have the risk of molten steel plugging leakage holes. From the viewpoint of obtaining the best comprehensive mechanical properties, a suitable content range of C is set to 1.5% to 3.9%, and a preferred range is 1.5% to 3.5%, and a suitable content range of N is 0.2% or less, within which the maximum wear resistance and the combination of toughness can be obtained.
Si is used as a deoxidizer and a matrix-strengthening element, but too high Si causes an increase in matrix brittleness, so that the content of Si is suitably in the range of 0.4% to 1.2% in the present invention.
Mn is added as a deoxidizer to weaken the harmful effect of S, and proper Mn also increases hardenability, but too high Mn increases the risk of brittleness, so that in the present invention, Mn is suitably contained in the range of 0.3% to 1.0%, and preferably in the range of 0.3% to 0.8%.
Cr is mainly used in the present invention to improve the matrix hardenability, and a suitable content range of Cr is 4% -7%.
Mo is used to increase hardenability to promote the desired hardness after heat treatment, and a suitable content range of Mo is 1.0% -3%.
Ti reacts with C or N to form high-hardness Ti-rich MX carbide, the micro-hardness of the high-hardness Ti-rich MX carbide reaches more than HV3000 and is obviously higher than other types of carbide and most of hard particles possibly causing abrasion, so that the effect of better protecting a matrix can be realized under the condition of an abrasion working condition, and the abrasion resistance is improved. The Ti-rich MX carbide does not have the risk of surface falling in a manner similar to TiC or TiN coated on the surface in the presence of a matrix, and based on a powder metallurgy process, the Ti-rich MX carbide can be uniformly distributed in the whole matrix from outside to inside in the form of fine approximately spherical particles and can stably play a role in the whole life cycle of a workpiece in the using process. Since too high Ti forms a large amount of high-melting carbide to cause the gas atomization milling process to become unstable, the content of Ti is suitably in the range of 0.5% to 6%, preferably in the range of 0.5% to 3% in the present invention.
In principle, V can be replaced by Ti in whole or in part, and the content of V should be as low as possible in consideration of cost performance, but according to the design concept of the invention, although the effectiveness of V-rich MX carbide on improving the wear resistance is relatively poor, the risk of steel blockage in the gas atomization powder preparation process caused by the V element is low, so the V alloy element can be used as a supplement to be matched with the Ti alloy element to meet the requirement of extremely high wear resistance. In the invention, the proper content range of V is less than or equal to 15 percent, and the total mass fraction of V and Ti is 5 to 16 percent.
In addition to the above-mentioned set chemical composition, the wear-resistant tool steel of the present invention, the balance being the Fe matrix, of course, includes some inevitable residual trace elements, including O, S, P, etc., and in order to prevent adverse effects on the mechanical properties of the alloy, it is required that the appropriate content range of O be 0.03% or less, the appropriate content range of S be 0.3% or less, and the appropriate content range of P be 0.05% or less.
In addition, in the chemical composition of the present invention, the impurities may further include at least one of Zr, Mg, Al, Co, Cu, Ni, Sn, and Pb, and the total amount of these impurities is not more than 1%.
By selecting proper chemical components and proportion, the volume fraction of high-hardness Ti-rich MX carbides in the tool steel is 1-15%, the grain size of the Ti-rich MX carbides in the tool steel is less than or equal to 7 microns, the grain size of at least 80% of the Ti-rich MX carbides in the tool steel is less than or equal to 3 microns, and the Ti-rich MX carbides in the tool steel are approximately spherical particles.
As a preferred possible embodiment, the wear-resistant tool steel of the present invention is prepared by a rapid solidification process to avoid segregation of alloying elements, such as a powder metallurgy process or a spray forming process, and the present invention preferably employs a powder metallurgy process. The main preparation process of the powder metallurgy process comprises gas atomization powder preparation, hot isostatic pressing and the like, and the spray forming process directly atomizes and sprays the alloy melt into an ingot. In order to further improve the mechanical properties or to achieve a product size of a specific shape, it is of course possible to further hot-deform the ingot.
It should be noted that the gas atomization powder preparation process of the present invention includes the following steps and process parameters:
a. the alloy is filled into a smelting ladle and is powered and heated under the protective atmosphere;
b. after the alloy is melted, continuously heating to more than or equal to 1600 ℃, sampling and analyzing components, and adjusting to a qualified range;
c. preheating an atomization tundish crucible in advance, wherein the temperature of the tundish before the alloy solution is atomized reaches 900-1300 ℃, and the superheat degree of the alloy melt is controlled at 100-300 ℃;
d. starting high-pressure nitrogen or argon and an evacuation fan after the temperature of the alloy melt meets the requirement, enabling the alloy melt to enter an atomization system through a ceramic eyelet at the bottom of a tundish, starting atomization of the alloy melt, and controlling the atomization flow of the alloy melt to be 10kg/min-50 kg/min;
e. conveying the atomized powder to a powder collecting tank body through air flow, and cooling to be less than or equal to 50 ℃.
In addition, the hot isostatic pressing process comprises the following steps:
a. placing the alloy powder prepared by the gas atomization powder making process in a metal sheath, vacuumizing the metal sheath, discharging gas in the sheath, and then welding and sealing;
b. and placing the powder-filled and sealed sheath in a hot isostatic pressing furnace, and realizing the complete densification of the powder in the sheath under the conditions that the temperature exceeds 1000 ℃ and the pressure exceeds 100MPa to form a hot isostatic pressing ingot.
In addition, the hot deformation is to further improve the mechanical property or realize the product size with a specific shape, and the ingot prepared by the hot isostatic pressing process is further subjected to hot deformation processing, wherein the hot deformation processing temperature is 950-1180 ℃.
Compared with the prior art, the invention has the following advantages:
the key point of the realization of the wear resistance of the wear-resistant tool steel is to select proper chemical components and proportion to form high-hardness Ti-rich MX carbide, the microhardness of the carbide reaches over HV3000 and exceeds the hardness of most of the existing metal or nonmetal hard abrasive particles, so that the effect of improving the wear resistance is achieved, and meanwhile, the wear resistance has higher cost performance.
In addition, the wear-resistant tool steel is prepared by adopting proper chemical components and proportions and combining a rapid solidification process, so that alloy element segregation can be effectively prevented, and high-hardness Ti-rich MX carbides in the steel are distributed in a matrix in a fine dispersion manner, so that the wear resistance can be improved, and the machinability cannot be damaged too much.
In addition, the wear-resistant tool steel is suitable for various cold working conditions including stamping, punching, powder pressing and the like, and is also suitable for manufacturing various wear-resistant parts such as an oil nozzle, a screw rod, a pump body sliding vane and the like based on the wear-resistant characteristic. It should be understood here that the above application is not a limitation on the scope of application of the invention, but serves to illustrate the mechanical properties of the invention, in addition to the wear resistance, the steel grade having at the same time the following performance characteristics: after heat treatment, the alloy has high toughness and hardness, small difference of different orientations of mechanical properties, small heat treatment deformation and easy grinding.
The achievement of one or more of the above properties depends on the selection of appropriate chemical components and proportions, and as a necessary condition, it employs a rapid solidification process to prepare ingots to avoid segregation of alloying elements.
Drawings
The accompanying drawings, which are incorporated in and constitute a part of this specification, illustrate an embodiment of the invention and, together with the description, serve to explain the invention and not to limit the invention. In the drawings:
FIG. 1 is a microstructure photograph of a wear-resistant tool steel according to example 1 of the present invention;
FIG. 2 is a microstructure picture of a wear-resistant tool steel according to example 2 of the present invention;
FIG. 3 is a microstructure picture of a wear-resistant tool steel according to example 5 of the present invention;
fig. 4 is a graphical representation of a comparison of the relative wear resistance of various embodiments of wear resistant tool steels according to the present invention.
Detailed Description
It should be noted that the embodiments and features of the embodiments may be combined with each other without conflict.
The present invention will be described in detail below with reference to the embodiments with reference to the attached drawings.
The chemical composition of the tool steel with the commercial grade of 10V and several specific examples of the invention are described below, and specific reference can be made to Table 1.
Table 1: chemical composition of various examples of tool steels
| Examples | C | Si | Mn | Cr | Mo | V | Ti |
| 1 | 2.45 | 0.8 | 0.5 | 5.25 | 1.3 | 9.75 | - |
| 2 | 1.8 | 0.6 | 0.5 | 5 | 1 | 6 | 0.5 |
| 3 | 3.9 | 0.9 | 0.5 | 5.5 | 2.5 | 15 | 1 |
| 4 | 1.5 | 0.4 | 0.3 | 4 | 3 | 3 | 3 |
| 5 | 1.7 | 1.2 | 1 | 7 | 2 | 0.01 | 6 |
| 6 | 1.9 | 0.8 | 0.8 | 5.5 | 2 | 2 | 3 |
| 7 | 2.6 | 0.8 | 0.8 | 5.5 | 2 | 7.5 | 1.7 |
| 8 | 3.4 | 0.8 | 0.8 | 5.5 | 2 | 15 | 0.3 |
| 9 | 2.5 | 0.8 | 0.8 | 5.5 | 2 | 0.01 | 7 |
In table 1, example 1 is a comparative example, which is a chemical composition of a tool steel of commercial grade 10V, and examples 2 to 9 are wear-resistant tool steels of the present invention. Examples 1 to 9 were all prepared by a powder metallurgy process, wherein a powder was prepared by a gas atomization powder preparation process, and then the powder was subjected to hot isostatic pressing densification to prepare an ingot blank with a diameter of 120mm, and further subjected to hot deformation processing to obtain a bar with a diameter of 50 mm.
The atomization powder preparation process comprises the following steps and process parameters:
a. the alloy is filled into a smelting ladle and is powered and heated under the protective atmosphere;
b. after the alloy is melted, the temperature is continuously raised to 1800 ℃, and after sampling and analyzing the components, the components are adjusted to a qualified range;
c. preheating an atomization tundish crucible, wherein the temperature of the tundish reaches 1000 ℃ before the molten alloy is atomized;
d. starting high-pressure nitrogen or argon and an evacuation fan after the temperature of the alloy melt meets the requirement, enabling the alloy melt to enter an atomization system through a ceramic eyelet at the bottom of a tundish, starting atomization of the alloy melt, and controlling the atomization flow of the alloy melt to be 20 kg/min;
e. conveying the atomized powder to a powder collecting tank body through air flow, and cooling to 50 ℃.
The hot isostatic pressing process comprises the following steps:
a. placing the alloy powder prepared by the gas atomization powder making process in a metal sheath, vacuumizing the metal sheath, discharging gas in the sheath, and then welding and sealing;
b. and placing the powder-filled and sealed capsule in a hot isostatic pressing furnace, and completely densifying the powder in the capsule at the temperature of 1100 ℃ and under the pressure of 110MPa to form a hot isostatic pressing ingot.
It should be noted here that in example 9, since Ti was added excessively, the molten steel was easily clogged with the atomizing nozzle during the production process, and stable production was difficult.
Next, the tool steels of examples 1 to 8 in table 1 were subjected to comparative tests in the following respects: (1) microstructure after heat treatment; (2) heat treatment hardness; (3) wear resistance. The comparative results are as follows:
(1) microstructure after heat treatment
The alloys of examples 1 to 8 were heat-treated according to the process parameters shown in Table 2, and the microstructure was analyzed.
Table 2: carbide content and particle size comparison for each example
In table 2, after the tool steels of the examples were quenched and tempered, the structures of the tool steels consisted of martensite, a small amount of retained austenite, and a hard second phase, and the second phase was subjected to morphological analysis and classification and analysis of the volume content thereof by using a scanning electron microscope.
The alloy of example 1 has a typical powder metallurgy alloy microstructure, as shown in fig. 1, with a fine and uniformly distributed second phase. By energy spectrum analysis, the alloy carbide phase of example 1 is mainly V-rich MC carbide with volume fraction of 14% -22% and average grain size of carbide of 1-3 μm.
The alloys of examples 2 to 8 were prepared by a powder metallurgy process, wherein the microstructures of examples 2 and 5 are shown in fig. 2 and 3, respectively, and the carbides are distributed discretely, and the carbide particles are fine and uniformly distributed.
Through composition identification analysis, the alloys of examples 2 to 7 contain 1 to 10 volume percent of Ti-rich MX carbides, the grain size of the Ti-rich MX carbides is less than or equal to 7 μm, at least 80 percent of the Ti-rich MX carbides has the grain size of less than or equal to 3 μm, and the shape of the Ti-rich MX carbides is similar to spherical grains. The high-hardness Ti-rich MX carbide is distributed in the matrix in a fine dispersion mode, so that the wear resistance can be improved, and the processability cannot be excessively damaged.
In the alloy of example 8, too little Ti-rich MX carbide phase was detected due to the small amount of Ti added, and the improvement of wear resistance was limited.
(2) Hardness by heat treatment
The alloys of examples 1 to 8 were heat treated according to the process parameters in table 3 and tested for hardness.
Table 3: hardness test results after Heat treatment of examples
Hardness tests of various heat-treated examples are carried out according to GB/T230.1-2018, and results show that the wear-resistant tool steel and the tool steel with the commercial grade of 10V can reach a high hardness level, and the requirements of most wear-resistant working conditions on material hardness can be met.
(3) Wear resistance
The wear resistance of the alloy is tested by a metal-to-metal wear test, the friction pair is 45# steel, the load is 50kg, and the revolution is 200 r/min. The process parameters for the heat treatment of the tool steels of examples 1 to 8 are shown in table 3. The wear resistance is measured according to the weight loss of the tested material and divided into 10 wear resistance grades, wherein 1 is the worst wear resistance and 10 is the best wear resistance.
Comparative results as shown in fig. 4, of examples 2 to 7, example 5 has a relatively high Ti alloy content and is matched with a corresponding C content designed to form a Ti-rich MX carbide structure, which shows the most excellent wear resistance, and example 8 alloy, because of too little Ti addition, has no significant improvement in wear resistance compared to example 1.
Generally, the alloy is a complex system, various alloy elements can interact with each other, so that various chemical components can simultaneously participate in one or more reactions and influence each other, taking C in TiC as an example, the C has the functions of solid solution in a matrix, promoting martensite formation and solid solution strengthening, participating in TiC combination reaction, participating in other carbide combination precipitation and the like, and in addition, the action part of N is similar to the C, so that the balance among various different reactions needs to be comprehensively considered, and the proper C alloy content and other alloy content need to be designed, so that TiC can be formed according to the required amount.
On the other hand, if the TiC is expected to play an effective role in the alloy, it is necessary to control the existence form of TiC, including the particle size, distribution, etc., the proper alloy composition and the combination of the rapid solidification process. Finally, the difficulty of process implementation needs to be considered, the design of excessively high TiC content cannot be implemented in production, and the wear-resisting effect is not obvious if the TiC content is too low.
In the description of the present specification, embodiments of the present invention have been given, it is to be understood that the above embodiments are exemplary and not to be construed as limiting the invention, and that one skilled in the art can combine, replace and modify the features of the various embodiments or examples described in the specification without contradiction.
Claims (10)
1. The wear-resistant tool steel is characterized by being prepared by adopting a rapid solidification process, and comprising the following chemical components in percentage by mass: c: 1.5% -3.9%, Si: 0.4% -1.2%, Mn: 0.3% -1.0%, Cr: 4% -7%, Mo: 1.0% -3%, V: less than or equal to 15 percent, Ti: 0.5 to 6 percent, and the balance of Fe and impurities.
2. A wear resistant tool steel according to claim 1, characterized in that: the chemical components of the material comprise the following components in percentage by mass: c: 1.5% -3.5%, Si: 0.4% -1.2%, Mn: 0.3% -0.8%, Cr: 4% -7%, Mo: 1.0% -3%, V: less than or equal to 15 percent, Ti: 0.5 to 3 percent.
3. A wear resistant tool steel according to claim 1, characterized in that: (V + Ti) ranges: 5 to 16 percent.
4. A wear resistant tool steel according to claim 1, characterized in that: the impurities include O, and O: less than or equal to 0.03 percent.
5. A wear resistant tool steel according to claim 1, characterized in that: the impurities include S, and S: less than or equal to 0.3 percent.
6. A wear resistant tool steel according to claim 1, characterized in that: the impurities include P, and P: less than or equal to 0.05 percent.
7. A wear resistant tool steel according to claim 1, characterized in that: the rapid solidification process includes a powder metallurgy process or a spray forming process.
8. A wear resistant tool steel according to claim 1, characterized in that: the volume fraction of Ti-rich MX carbide in the wear-resistant tool steel is 1-15%.
9. The wear resistant tool steel of claim 8, wherein: the grain size of the Ti-rich MX carbide is less than or equal to 7 mu m.
10. A wear resistant tool steel according to claim 9, characterized in that: at least 80% of the Ti-rich MX carbides have a particle size of less than or equal to 3 μm.
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| CN202110303425.XA Pending CN114318133A (en) | 2021-03-22 | 2021-03-22 | Wear-resistant tool steel |
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| CN108118257A (en) * | 2017-12-19 | 2018-06-05 | 钢铁研究总院 | TiC particle strengthenings ferrite/bainite base wear-resisting steel plate and manufacturing method |
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| CN104894483A (en) * | 2015-05-15 | 2015-09-09 | 安泰科技股份有限公司 | Powder metallurgy wear-resistant tool steel |
| CN108118257A (en) * | 2017-12-19 | 2018-06-05 | 钢铁研究总院 | TiC particle strengthenings ferrite/bainite base wear-resisting steel plate and manufacturing method |
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