CN112501520A - Impact-resistant and smashing-resistant wear-resistant steel and preparation method thereof - Google Patents
Impact-resistant and smashing-resistant wear-resistant steel and preparation method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
- 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
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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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Abstract
本发明公开了一种耐冲砸耐磨钢及其制备方法，耐冲砸耐磨钢含有(质量百分数)：C：0.22％～0.38％、Si：0.1％～0.3％、Mn：0.25％～1.0％、Cr：2.1％～6.5％、Mo：0.9％～1.8％、W：0.2％～0.8％和V：0.2％～0.8％，余量由Fe和不可避免的杂质构成。制备方法为：配料后熔炼成钢锭，钢锭在高温下进行均质化，再经镦粗、拔长、退火及调质处理制得耐冲砸耐磨钢。本发明的耐冲砸耐磨钢，耐冲砸及耐磨性能优良，从成分角度实现了晶粒度的细化，利于使用常规生产手段实现产品的稳定试制；制备方法，工艺简单，与通用的H13钢热处理工艺匹配，极具应用前景。
The invention discloses an impact-resistant and wear-resistant steel and a preparation method thereof. The impact-resistant and wear-resistant steel contains (mass percentage): C: 0.22%-0.38%, Si: 0.1%-0.3%, Mn: 0.25%- 1.0%, Cr: 2.1% to 6.5%, Mo: 0.9% to 1.8%, W: 0.2% to 0.8%, V: 0.2% to 0.8%, and the balance consists of Fe and inevitable impurities. The preparation method is as follows: after ingredients are smelted into steel ingots, the steel ingots are homogenized at high temperature, and then upsetting, elongation, annealing and quenching and tempering are performed to obtain impact-resistant and wear-resistant steel. The impact-resistant and wear-resistant steel of the present invention has excellent impact resistance and wear resistance, realizes the refinement of the grain size from the perspective of composition, and is conducive to the use of conventional production means to achieve stable trial production of products; the preparation method is simple in process, and is generally The heat treatment process of H13 steel is matched, and it has great application prospects.
Description
Technical Field
The invention belongs to the technical field of alloy steel, and relates to impact-resistant and impact-resistant wear-resistant steel and a preparation method thereof.
Background
The wear-resistant steel mainly comprises martensitic wear-resistant steel, martensitic ferritic wear-resistant steel and martensitic austenitic wear-resistant steel. The martensitic wear resistant steels are of different kinds based on the contribution of the solid solution strengthened martensitic matrix to the wear resistance, or the toughness is improved by means of ferrite, or the toughness is improved by means of retained austenite, and the purpose of the second phase is to relieve the brittleness caused by work hardening of the martensitic structure. Ferrite and austenite are toughness phases and have excellent toughness improving effect.
The wear-resistant steel for mining machinery is large in size and specification, different from batch-produced rolled materials, the composition and structure regulation and control of the wear-resistant steel are capable of restricting the capacity of the wear-resistant steel exceeding import, the existing domestic wear-resistant steel lifting bar technology mainly adopts intermediate frequency furnace smelting and die casting, the specification of the lifting bar is directly formed, the surface quality is rough, the structure is columnar dendritic crystals, quenching and tempering heat treatment is not carried out, the hardness is low, the toughness is extremely low, and the performance is far lower than that of the imported lifting bar.
At present, the wear resistance and toughness of a martensite structure are improved by the following three ideas: (1) regulating the phase ratio of solid solution alloy elements to precipitated phases, and comprehensively improving the hardness and the wear resistance of the martensite matrix through nanoscale and submicron precipitated phases; (2) the nanometer and submicron precipitated phases are inhibited from being too fast and thick, Mo element with a proper ratio is added to refine carbide, and the wear resistance is improved; (3) the carbon content of the matrix is reduced, so that solid-solution carbon atoms are fully precipitated to form a nano phase, but the toughness is reduced by solid solution.
The existing solutions are:
(1) patent CN 201711144749 discloses a preparation method of an insert wear-resistant steel block, which focuses on designing an insert structure based on 38CrSi steel alloy components, and includes wear-resistant steel block machining, wear-resistant steel block heat treatment, and wear-resistant steel block surface treatment, so as to obtain a wear-resistant steel block finished product. The invention has the advantages of good wear resistance, accurate positioning and difficult falling, but does not have the performance advantages of outstanding material and process in use.
(2) The patent CN 201510962051 proposes a martensite-ferrite dual-phase wear-resistant steel plate and a preparation method thereof, the martensite-ferrite dual-phase wear-resistant steel plate comprises a martensite and ferrite dual-phase structure, wherein the volume fraction of the martensite structure is more than 90%, the hardness is between 480 HB and 560HB, and the martensite-ferrite dual-phase wear-resistant steel plate is prepared by adopting elements such as C, Si, Mn, P, S, Nb, V, Ti, Mo, Ni, Cr, Al, B, N, Fe and the like with specific dosage. The product has high hardness, good low-temperature toughness and wear resistance, and is beneficial to manufacturing mechanical parts under severe environment, especially under extremely low temperature condition, but the martensite ferrite dual-phase structure is only suitable for module production within 100mm thickness, and for wear-resistant steel for inserts, the common thickness is more than 200mm, which is not suitable.
(3) Patent CN 201110163309 proposes a martensite wear-resistant steel and its manufacturing method, which does not use precious alloy elements such as Mo and Ni, and the mechanical properties meet the national standards, and the manganese steel with higher corrosion resistance is significantly improved, the operation time or wear resistance can be improved by 1-3 times, the performance is considerable, the cost is low, but no alloy element for significantly improving wear resistance is added, only martensite is used to improve wear resistance, and the solid solution strengthening effect is limited.
(4) Patent CN 201710676555 proposes a steel for wear-resistant steel bars, which comprises the following components by weight percent: 0.55 to 0.65 percent of C; 0.2 to 0.4 percent of Si; 0.60 to 1.0 percent of Mn; 0.9 to 1.3 percent of Cr; 0.15 to 0.25 percent of Mo; 0.1 to 0.2 percent of V; 0.01 to 0.05 percent of Ti; s is less than or equal to 0.020%; p is less than or equal to 0.020 percent, which meets the requirement that the wear-resistant steel bar has higher strength, hardness, toughness and wear resistance in the using field of the rod mill, basically realizes the balance and compromise of hardness, hardenability, strength and toughness, but is medium carbon, has poor toughness and is not suitable for impact and smash resistant environment.
(5) Patent CN 201810160997 discloses a steel for wear-resistant steel bar, which comprises the following components by weight percent: 0.55 to 0.65 percent of carbon; 0.2 to 0.4 percent of silicon; 0.60 to 1.0 percent of manganese; 0.9 to 1.3 percent of chromium; 0.15 to 0.25 percent of molybdenum; 0.1 to 0.2 percent of vanadium; 0.01 to 0.05 percent of titanium; sulfur is less than or equal to 0.020%; phosphorus is less than or equal to 0.020%; the wear-resistant steel bar has high strength, hardness, toughness and wear resistance on the use site of the rod mill to a certain extent, basically realizes balance and consideration of hardness, hardenability, strength and toughness, but is completed by increasing Mo and V on the basis of CN 201710676555, and still has the problem of low impact toughness.
(6) Patent KR 10-2016-.
(7) Patent WO PCT/US2011/061810/US 12/956,590 discloses a wear resistant steel which, although its performance is better, has a greater risk of quench cracking due to its too high nickel content.
(8) The patent CN 201910970664 provides a high-wear-resistance martensite/austenite dual-phase wear-resistant steel plate and a manufacturing method thereof, wherein a certain volume fraction of residual austenite (10-35%) is introduced into the traditional martensite wear-resistant steel, so that when the toughness is low, the toughness can be improved, and meanwhile, the wear resistance can be increased; by forming the superhard (Ti, Mo) xC particles in the matrix, the wear resistance of a steel plate finished product can be improved, the abrasive is effectively prevented from being pressed into the steel plate matrix or from sliding on the surface of the steel plate matrix, and sharp corners of abrasive particles are passivated, so that the wear resistance of the steel plate is more than 1.8 times of that of the low-alloy martensite wear-resistant steel with the same hardness. Although the toughness can be improved by adding the residual austenite, the residual austenite is easily transformed into a high-stress martensite phase in a punching and smashing environment to cause local cracks, so that the component is not suitable for the production of the punching and smashing resistant lifting strip.
Therefore, the development of the impact-resistant and smashing-resistant wear-resistant steel which is low in cost and good in applicability (the preparation method can be suitable for thicker module production) is of practical significance.
Disclosure of Invention
The invention aims to overcome the defects in the prior art and provides the impact-resistant wear-resistant steel with low cost and good applicability (the preparation method can be suitable for thicker module production) and the preparation method thereof.
In order to achieve the purpose, the invention provides the following technical scheme:
the impact-resistant and smashing-resistant wear-resistant steel comprises the following components in percentage by mass:
c: 0.22% -0.38%, Si: 0.1-0.3%, Mn: 0.25% -1.0%, Cr: 2.1% -6.5%, Mo: 0.9% -1.8%, W: 0.2% -0.8% and V: 0.2 to 0.8 percent, and the balance of Fe and inevitable impurities.
C is a solid solution strengthening element and a precipitated phase forming element, and if C is less than 0.25%, the strength and wear resistance are insufficient, and if C is more than 0.38%, the steel sheet is resistant to impact and cracking. Si is a key element for improving the yield strength and the hardness of the steel, and if the Si is higher than 0.3%, the toughness is insufficient, and if the Si is lower than 0.2%, the hardness is insufficient. Mn is a key element for improving the wear resistance, and is more than 1 percent, so that segregation is easily formed, and the whole material is easy to break; if Mn is less than 0.45%, the wear resistance is insufficient. Cr is a key element for forming alloy carbide, if Cr is too high, the alloy carbide is too much, the toughness is not good, and if Cr is less than 6.1%, the wear resistance is not sufficient. Mo is a refining carbide element, Mo is higher than 1.2%, the Mo is excessive, the cost is increased, and Mo is lower than 0.9%, the carbide refining capacity is insufficient. W is a key element for forming the wear-resistant phase WC, the cost is too high if W is too high, and the wear-resistant phase is insufficient if W is less than 0.2 percent. S and P are harmful elements, and the lower the content, the better the content, but the limitation is at the domestic metallurgical level. The invention can realize the balance of good friction and wear performance and excellent impact toughness through the combination of elements in specific proportion.
W and Mo are effective elements for comprehensively improving the wear resistance, the high-temperature heat strength and the heat conductivity, WC is dispersed and precipitated to prevent crystal grains from coarsening, molybdenum and tungsten are added to form a fine dispersed WC wear-resistant precipitated phase, the precipitated phase is densely pinned around the fine crystal grains to prevent the crystal grains from growing, and VC is replaced by a strengthening part of WC, so that the wear-resistant steel has more excellent wear resistance and impact toughness, and in addition, W is used for replacing part of expensive V elements to reduce the cost of raw materials.
The mold steel is given the code GBL66, G is given the code "nation", BL is given the code "BILONG", that is, BILONG mold material technology (Nantong) Inc., and 66 is the serial number of steel.
As a preferred technical scheme:
the impact-resistant and smashing-resistant wear-resistant steel comprises the following components in percentage by mass:
c: 0.25% -0.38%, Si: 0.2-0.3%, Mn: 0.45-1.0%, Cr: 6.1% -6.5%, Mo: 0.9% -1.2%, W: 0.2% -0.6% and V: 0.2 to 0.5 percent, and the balance of Fe and inevitable impurities.
The impact-resistant and smashing-resistant wear-resistant steel comprises the following components in percentage by mass:
c: 0.26%, Si: 0.15%, Mn: 0.25%, Cr: 6.4%, Mo: 0.9%, W: 0.2% and V: 0.3%, and the balance of Fe and inevitable impurities. The protection scope of the present invention is not limited to this, and only one possible technical solution is given here, and those skilled in the art can adjust the content of each component within a certain range to adjust the product performance according to the actual requirement.
The impact-resistant and smashing-resistant wear-resistant steel is characterized in that the inevitable impurity is S, P, N, O, H.
The content of the element S, P, N, O, H is the same or different and is 1-200 ppm, and the content is not limited as long as the content of the elements is within an acceptable range.
The impact-resistant and smash-resistant wear-resistant steel has the grain size of more than ASTM 5 grade, the hardness of 40-50 HRC, the impact energy of a non-notch 7X 10X 55 type is more than 270J, and the relative sliding friction coefficient of silicon nitride and impact-resistant die steel is less than or equal to 0.1. The impact-resistant and smashing-resistant wear-resistant steel has excellent hardness, room-temperature frictional wear performance, impact toughness and the like, and has a wide application prospect.
The invention also provides a method for preparing the impact-resistant and smashing-resistant wear-resistant steel, which comprises the following steps:
(1) smelting: the ingredients are put into an electric arc furnace for smelting, after the components of the smelted alloy reach indexes, the molten steel is cast into a mold to form a steel ingot at the temperature of 1530-1560 ℃, and oxide skin and pit defects on the surface of the steel ingot are removed after demolding;
(2) high-temperature homogenization: heating the round steel ingot to 1250-1295 ℃, keeping the temperature for (0.8-1.2) multiplied by D hours, wherein D is the diameter size cm of the steel ingot to uniformly diffuse the components in the steel, and then cooling to the forging temperature of 1100 +/-10 ℃;
(3) upsetting: upsetting a steel ingot at 1100 +/-10 ℃ on a press along the height direction of the steel ingot to 50% of the height, finishing, and returning and heating for 1.5-2 hours; then carrying out secondary upsetting and finishing, returning to the furnace and preserving heat for 1.5-2 hours, and then carrying out tertiary upsetting and finishing, wherein the final forging temperature is kept above 820 ℃;
(4) drawing out: cogging, forging and drawing out the steel ingot subjected to three-time repeated upsetting to the final size to obtain a module, keeping the final forging temperature above 820 ℃, and cooling the steel ingot to 80 ℃ after drawing out;
(5) annealing: heating the module to 740 +/-10 ℃, annealing for 10-26 hours, and then cooling along with the furnace;
(6) quenching and tempering: heating the module to 1020-1080 +/-5 ℃, preserving heat for 3.0-6.5 hours, fully cooling the discharged water mist to room temperature, tempering for 9-11 hours at 540 +/-5 ℃, air-cooling to room temperature, tempering for 9-11 hours at 575 +/-5 ℃, discharging and air-cooling.
The above terminology is to be interpreted as follows:
steel ingot: molten steel is poured into a casting mold through a ladle and is solidified to form a steel ingot with a certain shape, and more circular ingots, square ingots and hexagonal ingots are used.
High-temperature homogenization: and (3) a heat treatment process for eliminating or reducing the structural state that the intragranular components are not uniform and deviate from balance under the actual crystallization condition by diffusion at high temperature, and improving the processing performance and the service performance of the alloy material.
Segregation: the distribution of each component element in the alloy is not uniform when the alloy is crystallized.
Upsetting: a forging step in which the height of the billet is reduced and the cross section is increased. The transverse mechanical property of the forge piece is improved, and the anisotropy is reduced; repeated upsetting and stretching are carried out to break up carbide in the alloy tool steel so as to ensure that the carbide is uniformly distributed.
Drawing out: the forging and forming process is characterized in that the cross section area is reduced, and the length is increased.
The preparation method disclosed by the invention is simple in process, is matched with the heat treatment process of H13 steel commonly used in the current market, and has a good popularization and application prospect.
As a preferred technical scheme:
the method as described above, wherein in the step (6), the heating is carried out in an electric furnace.
Has the advantages that:
(1) the hardness of the impact-resistant wear-resistant steel reaches an excellent level of H13, so that the impact-resistant wear-resistant steel not only has excellent frictional wear performance, but also has excellent impact toughness;
(2) the impact-resistant wear-resistant steel realizes the refinement of the grain size from the component angle, and is beneficial to realizing the stable trial production of products by using conventional production means;
(3) the impact-resistant wear-resistant steel has excellent product performance, the grain size is more than ASTM grade 5, the hardness is 40-50 HRC, the impact energy of a non-notch 7 multiplied by 10 multiplied by 55 type is more than 270J, and the relative sliding friction coefficient of silicon nitride and impact-resistant die steel is less than or equal to 0.1;
(4) the preparation method disclosed by the invention is simple in process, is matched with the heat treatment process of H13 steel commonly used in the current market, and has a good popularization and application prospect.
Drawings
FIG. 1 is a metallographic structure diagram of impact and impact resistant wear-resistant steel prepared in example 1;
FIG. 2 is a chart showing the results of the measurement of the coefficient of friction and wear of the impact and smash resistant wear-resistant steel prepared in example 1.
Detailed Description
The following further describes the embodiments of the present invention with reference to the attached drawings.
Examples 1 to 4
A preparation method of impact-resistant and smashing-resistant wear-resistant steel comprises the following steps:
(1) smelting: putting the ingredients into an electric arc furnace according to the proportion for smelting, controlling the temperature to be about 1520-1540 ℃ after metallurgical components meet the requirements, casting into round ingots with the diameter of 450mm multiplied by 2050mm, and removing the defects of oxide skins, pits and the like after the round ingots are demolded;
(2) high-temperature homogenization: heating a steel ingot with the diameter of 450mm multiplied by 2050mm to 1265 +/-10 ℃, preserving heat for 11 hours, then cooling the steel ingot to 1180 +/-10 ℃ along with a furnace to prepare for forging processing;
(3) upsetting: upsetting a 1180 ℃ steel ingot to 45% of the height along the height direction of the steel ingot, then finishing (namely, flattening irregular edges by using a press), returning to 1180 +/-10 ℃ for heating for 3 hours, then carrying out second upsetting and finishing, returning to 1180 +/-10 ℃ for preserving heat for 3 hours, then carrying out third upsetting and finishing, and keeping the final forging temperature above 870 ℃;
(4) drawing out: forging and drawing the steel ingot subjected to three times of repeated upsetting to obtain a final size of 325mm multiplied by 425mm multiplied by 1100mm (thickness multiplied by width multiplied by length), an effective size of 325mm, keeping the final forging temperature above 870 ℃, and cooling the steel ingot to about 70 ℃ after drawing;
(5) annealing: heating the module to 740 +/-10 ℃ for annealing for 10 hours, then carrying out furnace cold cutting to 500 ℃, and discharging and air cooling;
(6) quenching and tempering: heating the module in an electric furnace to 1038 +/-5 ℃ and preserving heat for 4 hours, discharging the module from the furnace, cooling the module by water mist to room temperature, tempering the module for 10 hours at 560 ℃, cooling the module in air to room temperature, tempering the module for 10 hours at 600 +/-5 ℃, discharging the module from the furnace and cooling the module in air.
The preparation processes of the examples 1 to 4 are basically the same, but are different only in the composition of each element of the mixture, and the composition of each element of the mixture of the examples 1 to 4 is shown in the following table 1, wherein the content of Fe is the balance, and the unit of the content of each element in the table is wt%;
TABLE 1
| C | Si | Mn | Cr | Mo | W | V | S | P | |
| Example 1 | 0.26 | 0.25 | 0.75 | 6.4 | 0.9 | 0.2 | 0.3 | 0.016 | 0.023 |
| Example 2 | 0.27 | 0.2 | 1.0 | 6.2 | 1.2 | 0.5 | 0.2 | 0.009 | 0.002 |
| Example 3 | 0.25 | 0.22 | 0.4 | 6.3 | 1.0 | 0.6 | 0.5 | 0.010 | 0.001 |
| Example 4 | 0.38 | 0.3 | 0.6 | 6.5 | 1.1 | 0.2 | 0.8 | 0.009 | 0.001 |
The performance tests of the impact and smash resistant wear-resistant steel prepared in the embodiments 1 to 4 specifically include a hardness test after hardening and tempering, a pattern impact power test of 7 × 10 × 55 without a notch, and a test of the friction and wear coefficient of the impact and smash resistant wear-resistant steel prepared in the embodiment 1, wherein the results of the hardness test (hardness unit is HRC) and the pattern impact power test (unit is J) are shown in table 2;
TABLE 2
The friction and wear coefficient test result chart of the impact and smash resistant wear resistant steel prepared in the embodiment 1 is shown in fig. 2, the friction and wear coefficient of the traditional die steel such as H13 steel and 8418 steel is 0.4-0.6, and the friction and wear coefficient of the test steel is remarkably reduced compared with the H13 steel and the 8418 steel, which indicates that the wear resistance is remarkably improved.
The metallographic structure diagram (400 times) of the impact-resistant and wear-resistant steel prepared in example 1 is shown in fig. 1, and it can be seen from fig. 1 that the densely dispersed precipitated phases are distributed at the matrix and the grain boundaries, and the precipitated phases are mainly metastable and stable carbides which have high hardness and are not easy to coarsen and play a role in improving wear resistance in use.
Comparative examples 1 to 4
The preparation method of the die steel is basically the same as that of the embodiment 1, and is different from the steps of proportioning each element composition, and the proportioning each element composition of the comparative examples 1-4 is shown in the following table 3, wherein the content of Fe is the balance, and the unit of each element content in the table is wt%;
TABLE 3
| C | Si | Mn | Cr | Mo | W | V | S | P | |
| Example 1 | 0.36 | 0.35 | 0.25 | 9.4 | 0.9 | 0.2 | 0 | 0.016 | 0.023 |
| Example 2 | 0.22 | 0.59 | 1.0 | 2.1 | 1.2 | 0 | 0.2 | 0.009 | 0.002 |
| Example 3 | 0.25 | 0.1 | 0.4 | 3.2 | 1.8 | 0 | 0.5 | 0.010 | 0.001 |
| Example 4 | 0.38 | 0.15 | 0.3 | 0 | 1.6 | 0.2 | 0.8 | 0.009 | 0.001 |
The die steels prepared in comparative examples 1 to 4 were subjected to the same performance test in the same manner, wherein the results of the hardness test (hardness in HRC) and the pattern impact energy test (in J) are shown in Table 4.
TABLE 4
| Hardness of | Sample ballistic work (J) | |
| Comparative example 1 | 43 | 222 |
| Comparative example 2 | 45.5 | 168 |
| Comparative example 3 | 43 | 267 |
| Comparative example 4 | 38 | 269 |
Analysis of examples 1 to 4 and comparative examples 1 to 4 revealed that only a combination of elements in a specific ratio can achieve both good frictional wear properties and superior impact toughness.
Proved by verification, the hardness of the impact-resistant and smashing-resistant wear-resistant steel reaches an excellent level of H13, and the impact-resistant and smashing-resistant wear-resistant steel not only has excellent frictional wear performance, but also has excellent impact toughness; the grain size is refined from the component angle, and the stable trial production of the product is realized by using a conventional production means; the product has excellent performance, the grain size is more than ASTM grade 5, the hardness is 40-50 HRC, the style impact energy of a non-gap 7 multiplied by 10 multiplied by 55 is more than 270J, and the relative sliding friction coefficient of silicon nitride and the anti-impact die steel is less than or equal to 0.1; the preparation method has simple process, is matched with the heat treatment process of H13 steel commonly used in the current market, and has good popularization and application prospect.
Although specific embodiments of the present invention have been described above, it will be appreciated by those skilled in the art that these embodiments are merely illustrative and various changes or modifications may be made without departing from the principles and spirit of the invention.
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Cited By (3)
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| CN114959498A (en) * | 2022-06-27 | 2022-08-30 | 枣庄学院 | Wear-resistant steel lining plate material for ball mill and manufacturing method thereof |
| CN115011867A (en) * | 2022-04-19 | 2022-09-06 | 清华大学 | High strength and toughness wear-resistant steel lining plate and preparation method thereof |
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| CN115011867A (en) * | 2022-04-19 | 2022-09-06 | 清华大学 | High strength and toughness wear-resistant steel lining plate and preparation method thereof |
| CN115011867B (en) * | 2022-04-19 | 2023-04-14 | 清华大学 | High-strength and tough wear-resistant steel liner and preparation method thereof |
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