CN115181926B - Cutting tool - Google Patents
Cutting tool Download PDFInfo
- Publication number
- CN115181926B CN115181926B CN202111051287.7A CN202111051287A CN115181926B CN 115181926 B CN115181926 B CN 115181926B CN 202111051287 A CN202111051287 A CN 202111051287A CN 115181926 B CN115181926 B CN 115181926B
- Authority
- CN
- China
- Prior art keywords
- powder
- composite
- amorphous alloy
- alloy powder
- tool
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
- 238000005520 cutting process Methods 0.000 title claims description 11
- 239000000843 powder Substances 0.000 claims abstract description 201
- 239000002131 composite material Substances 0.000 claims abstract description 96
- 229910000808 amorphous metal alloy Inorganic materials 0.000 claims abstract description 67
- 239000011248 coating agent Substances 0.000 claims abstract description 50
- 238000000576 coating method Methods 0.000 claims abstract description 50
- 239000000835 fiber Substances 0.000 claims abstract description 28
- 239000002184 metal Substances 0.000 claims abstract description 26
- 229910052751 metal Inorganic materials 0.000 claims abstract description 26
- 238000005728 strengthening Methods 0.000 claims description 15
- 229910000838 Al alloy Inorganic materials 0.000 claims description 13
- 239000000758 substrate Substances 0.000 claims description 10
- 238000007751 thermal spraying Methods 0.000 claims description 10
- 229920000049 Carbon (fiber) Polymers 0.000 claims description 6
- 239000004917 carbon fiber Substances 0.000 claims description 6
- 229910000975 Carbon steel Inorganic materials 0.000 claims description 5
- 239000010962 carbon steel Substances 0.000 claims description 5
- 239000010935 stainless steel Substances 0.000 claims description 5
- 229910001220 stainless steel Inorganic materials 0.000 claims description 5
- 229910000851 Alloy steel Inorganic materials 0.000 claims description 4
- 239000002245 particle Substances 0.000 claims description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 3
- 229910000881 Cu alloy Inorganic materials 0.000 claims description 3
- 229910000640 Fe alloy Inorganic materials 0.000 claims description 3
- 229910000990 Ni alloy Inorganic materials 0.000 claims description 3
- 239000010439 graphite Substances 0.000 claims description 3
- 229910002804 graphite Inorganic materials 0.000 claims description 3
- 229920002239 polyacrylonitrile Polymers 0.000 claims description 3
- 229910020630 Co Ni Inorganic materials 0.000 claims description 2
- 229910002440 Co–Ni Inorganic materials 0.000 claims description 2
- 229910018054 Ni-Cu Inorganic materials 0.000 claims description 2
- 229910018102 Ni-Mn-Al Inorganic materials 0.000 claims description 2
- 229910018481 Ni—Cu Inorganic materials 0.000 claims description 2
- 229910018548 Ni—Mn—Al Inorganic materials 0.000 claims description 2
- 229910004337 Ti-Ni Inorganic materials 0.000 claims description 2
- 229910004688 Ti-V Inorganic materials 0.000 claims description 2
- 229910011209 Ti—Ni Inorganic materials 0.000 claims description 2
- 229910010968 Ti—V Inorganic materials 0.000 claims description 2
- 229910052799 carbon Inorganic materials 0.000 claims description 2
- 235000013311 vegetables Nutrition 0.000 claims description 2
- 239000008188 pellet Substances 0.000 claims 1
- 239000011159 matrix material Substances 0.000 abstract description 15
- 238000005260 corrosion Methods 0.000 abstract description 7
- 230000007797 corrosion Effects 0.000 abstract description 7
- 238000005507 spraying Methods 0.000 description 16
- 230000000052 comparative effect Effects 0.000 description 13
- 238000012360 testing method Methods 0.000 description 10
- 229910045601 alloy Inorganic materials 0.000 description 9
- 239000000956 alloy Substances 0.000 description 9
- 238000007373 indentation Methods 0.000 description 9
- 230000002045 lasting effect Effects 0.000 description 8
- 230000003014 reinforcing effect Effects 0.000 description 8
- 238000000034 method Methods 0.000 description 7
- 239000013078 crystal Substances 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 238000004519 manufacturing process Methods 0.000 description 5
- 238000002156 mixing Methods 0.000 description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 4
- 238000007750 plasma spraying Methods 0.000 description 4
- 238000000498 ball milling Methods 0.000 description 3
- 229910010293 ceramic material Inorganic materials 0.000 description 3
- 238000010288 cold spraying Methods 0.000 description 3
- 239000007769 metal material Substances 0.000 description 3
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 3
- 230000003746 surface roughness Effects 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 2
- 238000004140 cleaning Methods 0.000 description 2
- 230000008021 deposition Effects 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 229920003023 plastic Polymers 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000005488 sandblasting Methods 0.000 description 2
- 230000008646 thermal stress Effects 0.000 description 2
- 229910052721 tungsten Inorganic materials 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 229910052727 yttrium Inorganic materials 0.000 description 2
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- 244000137852 Petrea volubilis Species 0.000 description 1
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000005238 degreasing Methods 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000010285 flame spraying Methods 0.000 description 1
- 238000011010 flushing procedure Methods 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 239000008187 granular material Substances 0.000 description 1
- 238000007542 hardness measurement Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 229910001338 liquidmetal Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000005300 metallic glass Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000007781 pre-processing Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 229910052709 silver Inorganic materials 0.000 description 1
- 239000004332 silver Substances 0.000 description 1
- 239000002904 solvent Substances 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 230000007847 structural defect Effects 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
- C23C4/06—Metallic material
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C24/00—Coating starting from inorganic powder
- C23C24/02—Coating starting from inorganic powder by application of pressure only
- C23C24/04—Impact or kinetic deposition of particles
Abstract
The present application provides a tool comprising: the tool comprises a tool matrix and a composite coating, wherein the composite coating is formed on the surface of the tool matrix by adopting composite powder, the composite powder comprises amorphous alloy powder and/or high-entropy amorphous alloy powder, the composite powder also comprises reinforced phase powder, and the reinforced phase powder comprises metal powder and/or fiber. The tool according to the application is permanently sharp and has corrosion resistance.
Description
Technical Field
The application relates to the technical field of cutters, in particular to a cutter and a manufacturing method thereof.
Background
The existing cutters are usually made of metal materials or ceramic materials, wherein the metal materials mainly comprise carbon steel, stainless steel, high-end alloy steel and the like, and the ceramic materials are mostly zirconia. Tools made of metallic materials are either prone to rust or not wear-resistant and cannot be kept sharp permanently. For example: the carbon steel cutter needs to be wiped off after each use, and cannot retain moisture; the stainless steel cutter has better rust resistance, but lower hardness, and the cutting edge is easy to wear, so that the sharpness is not durable enough; the high-end alloy steel has high price. However, the cutter made of ceramic materials is extremely hard and does not rust, but is quite fragile, and needs to be held and placed lightly, so that the lasting sharpness of the cutter still needs to be improved in the prior art.
Disclosure of Invention
It is therefore an object of the present application to provide a tool to solve the problem of prior art tools not being wear resistant.
The tool according to the present application comprises: the tool comprises a tool matrix and a composite coating, wherein the composite coating is formed on the surface of the tool matrix by adopting composite powder, the composite powder comprises amorphous alloy powder and/or high-entropy amorphous alloy powder, the composite powder also comprises reinforced phase powder, and the reinforced phase powder comprises metal powder and/or fiber. The tool according to the application is permanently sharp and has corrosion resistance.
Preferably, the fracture toughness value of the metal corresponding to the metal powder is not less than 15MPa/m 2 The fracture toughness value of the fiber is not less than 15Mpa/m 2 。
In an embodiment, when the composite powder includes an amorphous alloy powder and a reinforcing phase powder, the weight of the reinforcing phase powder is 10% -30% of the total weight of the composite powder, the weight of the amorphous alloy powder is 70% -90% of the total weight of the composite powder, and the sum of the weight percentages of the amorphous alloy powder and the reinforcing phase powder is 100%.
In an embodiment, the amorphous alloy powder includes at least one of Fe-based amorphous alloy powder, zr-based amorphous alloy powder, cu-based amorphous alloy powder, al-based amorphous alloy powder, mg-based amorphous alloy powder, and Ti-based amorphous alloy powder.
In an embodiment, the amorphous alloy powder includes at least one of Fe, zr, cu, al, mg and Ti and at least one of Si, P, B, and C. Alternatively, the amorphous alloy powder further includes at least one of Sn, ni, pb, zn, nd, ga, mo, hf, cr, ca and Y.
In an embodiment, the metal powder includes at least one of Fe powder, al powder, cu powder, ni powder, fe alloy powder, al alloy powder, cu alloy powder, and Ni alloy powder, and the fiber includes at least one of a metal fiber, a carbon fiber, a polyacrylonitrile fiber, and a graphite fiber.
In an embodiment, the particle size of the composite powder is 300-1000 mesh and the thickness of the composite coating is 100 μm-500 μm.
In an embodiment, the composite powder may include a high-entropy amorphous alloy powder and a strengthening phase powder including a metal powder and/or fiber, wherein a fracture toughness value of a metal corresponding to the metal powder is not less than 15Mpa/m 2 The fracture toughness value of the fiber is not less than 15Mpa/m 2 The weight of the strengthening phase powder accounts for 10% -30% of the total weight of the composite powder, the weight of the high-entropy amorphous alloy powder accounts for 70% -90% of the total weight of the composite powder, and the sum of the weight percentages of the high-entropy amorphous alloy powder and the strengthening phase powder is 100%.
In an embodiment, the high entropy amorphous alloy powder may include: mg, al, sc, ti, V, cr, mn, fe, co, ni, cu, zn, zr, nb, mo, sn, hf, ta, W, pb, si and B.
Detailed Description
The inventive concept of the present application will be described more fully hereinafter.
According to the application, the composite coating is arranged on the surface of the cutter, so that the cutter can be wear-resistant and durable sharp. The amorphous alloy is called liquid metal or metallic glass, has no structural defects such as crystal boundary, twin crystal, lattice defect, dislocation, stacking fault and the like, has no heterogeneous phase, precipitate, segregation and other component fluctuation, is a disordered structure, has no plastic deformation forms such as grain boundary sliding and the like when being subjected to external force, and has higher strength and hardness. Because of the absence of grains and grain boundaries, amorphous alloys are more corrosion resistant than crystalline metals, generally do not experience localized corrosion, and inhibit pitting. Therefore, by providing the surface of the tool with the amorphous coating, the hardness and strength of the tool can be improved, and the tool can be made to have a certain corrosion resistance.
However, the cutter with higher hardness is easy to collapse during use, so that in order to improve the wear resistance of the cutter and ensure the durable sharpness of the cutter, the cutter is required to have a certain degree of toughness, so that the cutter can bear the pressure and impact in the cutting process, and the cutter is prevented from being broken.
The toughness of a composite powder formed of an amorphous alloy or a high-entropy amorphous alloy can be further improved by adding a metal powder or a fiber having a certain toughness to the amorphous alloy or the high-entropy amorphous alloy powder. The composite powder is sprayed on a cutter matrix in a thermal spraying mode to form a composite coating with certain hardness and good toughness, so that the corrosion resistance and lasting sharpness of the cutter can be further improved.
According to an embodiment of the present application, there is provided a tool including: the tool matrix and the composite coating adopt composite powder to form the composite coating on the surface of the tool matrix in a spraying mode. Wherein the composite powder comprises amorphous alloy powder and reinforced phase powderThe powder comprises metal powder and/or fiber. Wherein the fracture toughness value of the metal corresponding to the metal powder is not less than 15Mpa/m 2 The fracture toughness value of the fiber is not less than 15Mpa/m 2 . The tool substrate may be stainless steel, alloy steel or carbon steel.
In an embodiment, toughness refers to the ability of a material to absorb energy during plastic deformation and fracture, the better the toughness, the less likely brittle fracture will occur. Fracture toughness value is not less than 15Mpa/m 2 The metal or fiber of the alloy has good toughness, and can improve the toughness of the composite powder, so that the formed composite coating has certain toughness.
In embodiments of the present application, the fibers may be in the form of strips, granules, or powder.
The spraying mode can be thermal spraying or cold spraying. Cold spraying is mainly by mechanical bonding of the composite powder to the tool substrate. The amorphous alloy powder has high hardness, low toughness and low deformation rate during cold spraying, so that the deposition amount is small. In order to improve the deposition efficiency of the composite powder and the utilization rate of raw materials, thermal spraying is preferably adopted.
According to the embodiment of the application, the composite coating is formed by the amorphous alloy powder and the metal powder and/or the fiber serving as the reinforcing phase powder, and the cutter has higher hardness due to the amorphous structure contained in the composite coating, and the toughness of the composite coating can be improved due to the fact that the crystal particles or the fiber with toughness are uniformly dispersed in the amorphous structure of the composite coating, so that the formed cutter has enough hardness and toughness, can resist abrasion and meets the lasting sharpness requirement.
In some embodiments, the weight of the strengthening phase powder is 10% -30% of the total weight of the composite powder, the weight of the amorphous alloy powder is 70% -90% of the total weight of the composite powder, and the sum of the weight percentages of the amorphous alloy powder and the strengthening phase powder is 100%. In the embodiment of the present application, the weight of the reinforcing phase powder may be 15%, 20% or 25% of the weight of the composite powder, and the present application is not limited thereto.
In these examples, if the weight of the reinforcing phase powder is less than 10%, the toughness improvement of the formed composite coating is not significant. If the weight of the reinforcing phase powder is more than 30%, the toughness is improved, but the hardness of the formed composite coating is lowered, so that the durability sharpness of the formed cutter is lowered.
In some embodiments, the amorphous alloy powder comprises: fe-based amorphous alloy powder, zr-based amorphous alloy powder, cu-based amorphous alloy powder, al-based amorphous alloy powder, mg-based amorphous alloy powder, ti-based amorphous alloy powder, the amorphous alloy powder of the present application may include one or more of the above 6 amorphous alloy powders. Amorphous alloy powders in the same series (e.g., fe-based amorphous alloy powders) have a small difference in melting point, such as, but not limited to: the temperature is less than 20 ℃, and a plurality of amorphous alloy powders in the same series can be selected for mixing so as to avoid the mutual mixing of amorphous alloys in different series, and the process parameters are different, so that the quality of the formed composite coating is poor.
Further, the amorphous alloy powder includes: fe. Zr, cu, al, mg and Ti as a base metal element; and at least one of nonmetallic Si, P, B, and C as an auxiliary element.
In addition, the amorphous alloy powder may further include: sn, ni, pb, zn, nd, ga, mo, hf, cr, ca, Y.
As an example, the amorphous alloy may include: zr60-Cr20-Al13-Ni5-Hf2; zr65- (Ti) -Ni10-Al10-Cu15; fe80-Cr5-Mo6-B4-Si5; fe50-Zr20-Cr9-B6-Cu10-Y5.Fe80-Cr5-Mo6-B4-Si5, fe85-Si8-B5-Cr2-C5.
In some embodiments, the metal powder may include: at least one of Fe powder, al powder, cu powder, ni powder, fe alloy powder, al alloy powder, cu alloy powder and Ni alloy powder; the fiber may comprise: at least one of metal fibers, carbon fibers, polyacrylonitrile fibers and graphite fibers.
In some embodiments, the particle sizes of both the amorphous alloy powder and the strengthening phase powder may be: and (3) mixing the reinforced phase powder into amorphous alloy powder in a ball milling or granulating mode to form composite powder with 300-1000 meshes, and taking the composite powder as a spraying raw material for thermal spraying. In addition, the composite powder with the granularity of 200-600 meshes is sieved, if the composite powder is smaller than 200 meshes, the composite powder needs higher temperature to be fully heated and deformed, partial crystal forms can be converted, and if the composite powder is larger than 600 meshes, the powder is too fine, and the preparation cost is correspondingly increased.
In addition, when mixing is performed by ball milling or granulating, it is necessary to control the temperature of the ball milling or granulating process not to exceed the crystallization transition temperature of the amorphous alloy powder used.
In some embodiments, the thickness of the composite coating may be 100 μm to 500 μm. The thickness of the composite coating is too thin when the thickness is less than 100 mu m, the lasting sharpness life is shorter, and the thickness of the composite coating is too thick when the thickness is more than 500 mu m, so that the thermal stress of the composite coating and the cutter is increased, and the composite coating and the cutter are easy to deform or crack.
If the coating with the target thickness is sprayed at one time, the coating can be locally overheated due to the excessive thickness, so that the quality of the finally formed coating is affected. The target coating may be formed by multiple spraying, and illustratively, when the thickness of the composite coating is 500 μm, the final composite coating is formed by 10 spraying, and the thickness of each spraying is 50 μm, the quality of the composite coating may be further improved by multiple spraying, as compared to one-time spraying.
According to an embodiment of the present application, a method of manufacturing a cutter includes: before spraying, cleaning, degreasing and sand blasting are carried out on the cutter matrix, and the surface roughness after sand blasting is 2-4 mu m so as to improve the bonding firmness of the cutter matrix and the composite coating; and preheating the tool substrate at a temperature, for example, the preheating temperature can be 200-300 ℃, preferably can be 250 ℃, the preheating can reduce the temperature difference between the tool substrate and the high-temperature composite powder, reduce the thermal stress between the tool substrate and the composite coating, and improve the quality and the bonding strength of the coating.
According to an embodiment of the present application, the method of manufacturing a cutter may further include: forming a composite coating on the surface of the tool substrate by thermal spraying using a composite powder, wherein the thermal spraying uses low pressure plasma spraying, and parameters of the plasma spraying are as follows: vacuum of spray boothPumping to 2-4Pa, and then flushing argon to 4X 10 3 -8×10 3 Pa, transferring arc power of 20-40Kw, arc current of 500-700A, spraying distance of 100-150mm, spraying angle of 60-80 degrees, powder feeding speed: 20-50g/min, hydrogen pressure: 0.3-0.7MPa, and flow rate is 5-10L/min.
According to an embodiment of the present application, the method of manufacturing a cutter may further include: after thermal spraying, the surface of the tool is treated, for example: and sanding the surface of the composite coating to obtain the surface roughness of the cutter of 1-2 mu m. If the roughness is lower than 1 mu m, the process difficulty is increased, and if the roughness is higher than 2 mu m, the surface smoothness is affected, and the vegetable cutting experience is reduced. Here, the roughness may be 1.5 μm.
According to an embodiment of the present application, the composite powder may include a high-entropy amorphous alloy powder and a reinforcing phase powder including: metal powder and/or fiber, and fracture toughness value of metal corresponding to the metal powder is not less than 15Mpa/m 2 The fracture toughness value of the fiber is not less than 15Mpa/m 2 。
In the embodiment of the application, the high-entropy alloy has a lattice distortion effect, when the atomic radius difference of several elements composing the high-entropy alloy is too large, the lattice distortion energy is too high to keep the crystal structure, an amorphous structure is formed, and the amorphous high-entropy alloy, namely the high-entropy amorphous alloy, has the atomic radius difference of the elements of the high-entropy alloy more than 12 percent. In the embodiment of the application, the preparation method of the high-entropy amorphous alloy powder can comprise an air atomization method and a rotating electrode method, and after the high-entropy amorphous alloy powder is prepared, the powder with 300-1000 meshes of granularity is sieved by a sieve, so that the high-entropy amorphous alloy powder is obtained.
In some embodiments, the weight of the strengthening phase powder is 10% -30% of the total weight of the composite powder, the weight of the high-entropy amorphous alloy powder is 70% -90% of the total weight of the composite powder, and the sum of the weight percentages of the high-entropy amorphous alloy powder and the strengthening phase powder is 100%.
In these examples, the weight of the strengthening phase powder is 10% -30% of the total weight of the strengthening phase powder and the high entropy amorphous alloy powder, and if the weight of the strengthening phase powder is less than 10%, the toughness improvement of the formed composite coating is not obvious, and if the weight of the strengthening phase powder is more than 30%, although the toughness is improved, the hardness of the formed composite coating is reduced, so that the lasting sharpness of the formed tool is reduced.
Further, the high-entropy amorphous alloy powder includes: mg, al, sc, ti, V, cr, mn, fe, co, ni, cu, zn, zr, nb, mo, sn, hf, ta, W, pb, si, B, wherein, when nonmetallic Si and/or B are selected, P and/or C may be substituted, and a high-entropy amorphous alloy is formed at an equiatomic ratio or approximately equiatomic ratio.
As an example, the high-entropy amorphous alloy powder may be a high-entropy equal-atomic-ratio amorphous alloy powder, for example, the high-entropy equal-atomic-ratio amorphous alloy includes Fe-Sn-Pb-P-C, al-Cr-Fe-Co-Ni, al-Cr-Fe-Ti-Ni, al-Cr-Fe-Co-Ni-Cu, fe-Ni-Al-Cr, fe-Cr-Ni-Mn-Al, fe-Cr-Cu-Ti-V.
In some embodiments, the tool substrate may be made of stainless steel material, and the tool substrate and the blade portion may be surface treated with a composite powder by thermal spraying to form the composite coating. The thermal spraying may be low pressure plasma spraying, supersonic flame spraying, arc spraying, etc.
The technical scheme of the present application will be described in detail with reference to examples, but the scope of the present application is not limited to the examples.
Example 1
The tool according to example 1 was prepared by the following method:
step S10, preprocessing the surface of the cutter matrix, specifically, cleaning the surface of the cutter matrix by adopting an alkaline solvent and clear water in sequence, and then drying;
step S20, preheating a cutter matrix by adopting a heating furnace, and preheating at a preheating temperature of 200 ℃;
s30, forming a composite coating on the surface of the cutter matrix by adopting composite powder through a low-pressure plasma spraying mode, wherein the composite powder is formed by mixing Fe80-Cr5-Mo6-B4-Si5 and Al alloy powder, and Al is mixedThe weight of the gold powder is 30% of the weight of the composite powder, and the weight of Fe80-Cr5-Mo6-B4-Si5 is 70% of the weight of the composite powder. The spraying parameters are as follows: the vacuum degree of the spraying chamber is 3Pa, and then argon is flushed to 6 multiplied by 10 3 Pa, transfer arc power 30Kw, arc current 600A, spraying distance 120mm, spraying angle 70 DEG, cutter matrix preheating temperature 200 ℃, powder feeding speed: 40g/min, hydrogen pressure: 0.5MPa, and the flow rate is 8L/min.
And S40, after the composite coating is sprayed, naturally cooling, sanding the surface by adopting 120-mesh sand paper, enabling the surface roughness Ra to reach 1-2 mu m after sanding, and sharpening the cutting edge part of the cutter to finish the manufacture of the cutter.
Example 2
A tool according to example 2 was manufactured in the same manner as in example 1, except that the weight of Al alloy powder in the composite powder was 20% by weight of the composite powder and the weight of Fe80-Cr5-Mo6-B4-Si5 was 80% by weight of the composite powder.
Example 3
A tool according to example 3 was manufactured in the same manner as in example 1, except that the weight of Al alloy powder in the composite powder was 10% by weight of the composite powder and the weight of Fe80-Cr5-Mo6-B4-Si5 was 90% by weight of the composite powder.
Example 4
A tool according to example 4 was manufactured in the same manner as in example 1, except that carbon fibers were used instead of Al alloy powder.
Example 5
A tool according to example 5 was manufactured in the same manner as in example 1, except that Cu powder was used instead of Al alloy powder.
Example 6
Except that Zr65-Ni10-Al10-Cu15 is adopted to replace Fe80-Cr5-Mo6-B4-Si5 and carbon fiber is adopted to replace Al alloy powder, the cutter according to example 6 was manufactured in the same manner as in example 1.
Example 7
Except that Zr65-Ni10-Al10-Cu15 is adopted to replace Fe80-Cr5-Mo6-B4-Si5, the tool according to example 7 was manufactured in the same way as in example 1.
Example 8
A tool according to example 8 was manufactured in the same manner as in example 1, except that the equal atomic ratio entropy alloy Fe-Si-B-Nb-Cu was used instead of Fe80-Cr5-Mo6-B4-Si5 and the weight of Fe-Si-B-Nb-Cu was 70% of the weight of the composite powder.
Example 9
A tool according to example 9 was manufactured in the same manner as in example 1, except that the equal atomic ratio entropy alloy Fe-Si-B-Nb-Cu was used instead of Fe80-Cr5-Mo6-B4-Si5 and carbon fiber was used instead of Al alloy powder.
Comparative example 1
A tool according to comparative example 1 was manufactured in the same manner as in example 1, except that cast iron powder was used instead of Al alloy powder.
Comparative example 2
A tool according to comparative example 2 was manufactured in the same manner as in example 1, except that the weight of the Al alloy powder was 40% of the weight of the composite powder and the weight of Fe80-Cr5-Mo6-B4-Si5 was 60% of the weight of the composite powder.
Comparative example 3
A tool according to comparative example 3 was manufactured in the same manner as in example 1, except that the weight of the Al alloy powder was 5% of the weight of the composite powder and the weight of Fe80-Cr5-Mo6-B4-Si5 was 95% of the weight of the composite powder.
Comparative example 4
A tool according to comparative example 4 was manufactured in the same manner as in example 1, except that only Fe80-Cr5-Mo6-B4-Si5 was used without adding the strengthening phase powder.
Comparative example 5
Commercial carbon steel cutters.
The compositions according to the application of examples 1 to 9 and comparative examples 1 to 5 are given in the following Table 1:
table 1 parameters of examples and comparative examples of the present application
Performance index test
The test results of examples 1-9 and comparative examples 1-5 are shown in Table 2, and the specific performance test methods are as follows:
(1) Coating hardness testing method:
cutting, embedding and polishing the composite coating of the cutter to prepare a metallographic specimen. And (3) placing the metallographic specimen on a Vickers hardness tester, measuring the hardness of the section of the composite coating, and testing ten points to calculate the average value as the hardness of the measured composite coating.
(2) The durable sharpness testing method comprises the following steps:
the cutting edge of the tested cutter is fixed on the cutter fixing device horizontally downwards, and after the weight is added, the cutter is pressed on the simulant with the pressure of 16N. The simulated object is cut, the simulated object is cut for 100mm, the simulated object is cut for 5 times, and then the cutter is cut, and the lasting sharpness of the cutter is judged by adopting an evaluation object. And (3) stopping the test until the evaluation object is not cut, and recording the total cutting times from the start to the stop of the test, namely, the lasting sharpness of the cutter, wherein the longer the total cutting times are, the higher the lasting sharpness is.
(3) The toughness testing method comprises the following steps: by indentation
The test pieces were cut, inlaid and polished to a mirror surface. The test platform is a silver-coated HV5 small-load Vickers hardness tester, and a total of 10 indentations are made on the cross section at intervals under the load of 5 kg. The diagonal line of the indentation is required to be parallel to the bonding surface of the coating matrix, a sufficient distance is required between cracks generated by the two indentations, the cracks cannot interfere with each other, and finally, half a length of the diagonal line of the indentation and the length c of the cracks of the indentation are read under a metallographic microscope. And finally, calculating the cracking toughness of the coating according to a Wilshaw formula, and taking the average value of the calculation results of 10 indentations as the final result.
Wilshaw formula:
wherein P is load and N; a is half the diagonal length of the indentation, μm; c is the distance from the centre of the indentation to the end of the crack, μm.
Table 2: schematic table of test results of examples and comparative examples of the present application
From the above, it can be seen from table 2 that: the cutters of the embodiments 1-9 have better hardness and toughness, can meet the requirement of wear resistance, can be sharp for a long time, have better corrosion resistance, and can inhibit the rust of the cutters.
Although embodiments of the present application have been described in detail hereinabove, various modifications and variations may be made to the embodiments of the application by those skilled in the art without departing from the spirit and scope of the application. It will be appreciated that those skilled in the art will appreciate that such modifications and variations will still fall within the spirit and scope of the embodiments of the application as defined by the appended claims.
Claims (10)
1. A cutter for cutting vegetables, the cutter comprising: the tool substrate and the composite coating are formed on the surface of the tool substrate by adopting composite powder, wherein the composite powder comprises high-entropy equal-atomic-ratio amorphous alloy powder and reinforced phase powder with toughness mixed in the high-entropy equal-atomic-ratio amorphous alloy powder, the reinforced phase powder comprises metal powder and/or fiber, and the fracture toughness value of metal corresponding to the metal powder is not less than 15Mpa/m 2 The fiber has a fracture toughness value not smaller than that of the fiberAt 15Mpa/m 2 The high-entropy equal-atomic-ratio amorphous alloy powder comprises: at least one of Fe-Sn-Pb-P-C, al-Cr-Fe-Co-Ni, al-Cr-Fe-Ti-Ni, al-Cr-Fe-Co-Ni-Cu, fe-Ni-Al-Cr, fe-Cr-Ni-Mn-Al, fe-Cr-Cu-Ti-V, and Fe-Si-B-Nb-Cu;
wherein the weight of the strengthening phase powder accounts for 10% -30% of the total weight of the composite powder, the weight of the high-entropy amorphous alloy powder accounts for 70% -90% of the total weight of the composite powder, and the sum of the weight percentages of the high-entropy amorphous alloy powder and the strengthening phase powder is 100%.
2. The tool according to claim 1, wherein,
the metal powder includes at least one of Fe powder, al powder, cu powder, ni powder, fe alloy powder, al alloy powder, cu alloy powder and Ni alloy powder.
3. The cutter of claim 1, wherein the fibers comprise at least one of metal fibers, carbon fibers, polyacrylonitrile fibers, and graphite fibers.
4. The tool according to claim 1, wherein the composite powder has a particle size of 300-1000 mesh.
5. The tool according to claim 1, wherein the thickness of the composite coating is 100 μm-500 μm.
6. The tool according to claim 1, wherein the tool body is made of stainless steel, alloy steel or carbon steel.
7. The tool of claim 1, wherein the composite coating is formed by thermal spraying.
8. The tool according to claim 1, wherein the atomic radius difference between the elements forming the high entropy equal atomic ratio amorphous alloy powder is more than 12%.
9. The tool according to claim 1, wherein the roughness Ra value of the composite coating surface is 1 μm-2 μm.
10. The tool according to claim 1, wherein the fibres are in the form of strips and/or pellets.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202111051287.7A CN115181926B (en) | 2021-09-08 | 2021-09-08 | Cutting tool |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202111051287.7A CN115181926B (en) | 2021-09-08 | 2021-09-08 | Cutting tool |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN115181926A CN115181926A (en) | 2022-10-14 |
| CN115181926B true CN115181926B (en) | 2023-12-01 |
Family
ID=83511208
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202111051287.7A Active CN115181926B (en) | 2021-09-08 | 2021-09-08 | Cutting tool |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115181926B (en) |
Citations (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103252495A (en) * | 2013-05-03 | 2013-08-21 | 中国人民解放军装甲兵工程学院 | Fabrication method of high-entropy alloy coating containing amorphous nanocrystalline |
| CN103589882A (en) * | 2013-12-02 | 2014-02-19 | 东南大学 | Blocky high-entropy metallic glass and preparation method thereof |
| CN103866223A (en) * | 2013-09-26 | 2014-06-18 | 华中科技大学 | Novel tough particle strengthened iron-based amorphous composite coating |
| TWM547465U (en) * | 2017-05-14 | 2017-08-21 | 國立臺灣科技大學 | Knife |
| CN207120532U (en) * | 2017-05-24 | 2018-03-20 | 朱瑾 | Cutter |
| CN108866481A (en) * | 2018-06-06 | 2018-11-23 | 广东工业大学 | A kind of nano combined Al-Ti-V-Cu-N coating and its preparation method and application |
| CN109439995A (en) * | 2018-12-29 | 2019-03-08 | 宝钢轧辊科技有限责任公司 | High entropy amorphous alloy coating and preparation method thereof |
| CN110106473A (en) * | 2019-05-22 | 2019-08-09 | 江苏理工学院 | A kind of high entropy noncrystal membrane and preparation method and application |
| CN110295347A (en) * | 2019-06-14 | 2019-10-01 | 东莞职业技术学院 | A method of using high-entropy alloy plated film on cutter |
| CN110453171A (en) * | 2019-09-10 | 2019-11-15 | 安徽工业大学 | A kind of amorphous coating, matrix and its preparation process with the coating |
| CN110699629A (en) * | 2019-11-01 | 2020-01-17 | 河海大学 | High-entropy amorphous powder with high-temperature erosion resistance and plasma spraying function, coating of high-entropy amorphous powder, preparation method of coating and application of coating |
| CN110923481A (en) * | 2018-09-20 | 2020-03-27 | 天津大学 | Amorphous film/high-entropy alloy composite material and preparation method thereof |
-
2021
- 2021-09-08 CN CN202111051287.7A patent/CN115181926B/en active Active
Patent Citations (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103252495A (en) * | 2013-05-03 | 2013-08-21 | 中国人民解放军装甲兵工程学院 | Fabrication method of high-entropy alloy coating containing amorphous nanocrystalline |
| CN103866223A (en) * | 2013-09-26 | 2014-06-18 | 华中科技大学 | Novel tough particle strengthened iron-based amorphous composite coating |
| CN103589882A (en) * | 2013-12-02 | 2014-02-19 | 东南大学 | Blocky high-entropy metallic glass and preparation method thereof |
| TWM547465U (en) * | 2017-05-14 | 2017-08-21 | 國立臺灣科技大學 | Knife |
| CN207120532U (en) * | 2017-05-24 | 2018-03-20 | 朱瑾 | Cutter |
| CN108866481A (en) * | 2018-06-06 | 2018-11-23 | 广东工业大学 | A kind of nano combined Al-Ti-V-Cu-N coating and its preparation method and application |
| CN110923481A (en) * | 2018-09-20 | 2020-03-27 | 天津大学 | Amorphous film/high-entropy alloy composite material and preparation method thereof |
| CN109439995A (en) * | 2018-12-29 | 2019-03-08 | 宝钢轧辊科技有限责任公司 | High entropy amorphous alloy coating and preparation method thereof |
| CN110106473A (en) * | 2019-05-22 | 2019-08-09 | 江苏理工学院 | A kind of high entropy noncrystal membrane and preparation method and application |
| CN110295347A (en) * | 2019-06-14 | 2019-10-01 | 东莞职业技术学院 | A method of using high-entropy alloy plated film on cutter |
| CN110453171A (en) * | 2019-09-10 | 2019-11-15 | 安徽工业大学 | A kind of amorphous coating, matrix and its preparation process with the coating |
| CN110699629A (en) * | 2019-11-01 | 2020-01-17 | 河海大学 | High-entropy amorphous powder with high-temperature erosion resistance and plasma spraying function, coating of high-entropy amorphous powder, preparation method of coating and application of coating |
Also Published As
| Publication number | Publication date |
|---|---|
| CN115181926A (en) | 2022-10-14 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN106119838B (en) | Cutter for strengthening cutting edge by laser cladding technology | |
| KR102268620B1 (en) | Ultra-high-speed laser cladding iron-based metal powder, and preparation method and application thereof | |
| CN101519778B (en) | Laser cladding method for strengthening surface of piercing point | |
| US11850659B2 (en) | High entropy alloy powder for laser cladding and application method thereof | |
| CN108866538B (en) | Laser cladding in-situ synthesis composite carbide (Ti, Nb) C reinforced Ni-based coating and preparation | |
| CN113832461B (en) | Nickel-based alloy powder for laser cladding, ceramic particle reinforced composite powder and application | |
| CN113445041B (en) | Preparation method of low-cost light high-entropy alloy/aluminum oxide composite coating on surface of magnesium alloy | |
| CN102453902A (en) | Method for preparing tungsten carbide hard alloy coating on surface of high-speed wire roller collar | |
| CN113319272B (en) | Metal ceramic powder material for wear-resistant layer of section steel conveying roller and manufacturing method of wear-resistant layer | |
| CN110804711A (en) | High-entropy alloy powder and preparation method and application of laser cladding layer | |
| CN109881109B (en) | Laser cladding material and preparation method of laser cladding coating | |
| KR101563533B1 (en) | Ni-Cr-Co-BASED ALLOY HAVING HIGH-TEMPERATURE CORROSION RESISTANCE PROPERTIES, AND POPPET VALVE HAVING SURFACE MODIFIED WITH SAME | |
| CN106756997A (en) | A kind of ceramic reinforced Metal Substrate laser cladding layer and its preparation technology | |
| CN111850374B (en) | High-entropy alloy powder for laser cladding and coating preparation method | |
| CN115386779B (en) | Ceramic phase and high-melting-point phase synergized high-entropy alloy coating and preparation method thereof | |
| CN115181926B (en) | Cutting tool | |
| CN116555758B (en) | Metal ceramic gradient coating and preparation method and application thereof | |
| CN110923707B (en) | Titanium alloy surface high-temperature-resistant composite coating material based on laser cladding | |
| CN110760837A (en) | Steel surface laser cladding ceramic reinforced Ni-based composite coating and preparation method thereof | |
| CN115074724A (en) | V-element-reinforced Ni-based wear-resistant laser cladding coating and preparation method thereof | |
| CN114457272A (en) | High-entropy alloy and method for repairing tungsten-based powder alloy die-casting die by laser cladding | |
| CN111593339B (en) | Multilayer high-entropy alloy laser cladding layer containing nano tantalum carbide and preparation method thereof | |
| Simson et al. | Optimization of reinforcement content of powder metallurgy hardfacings in abrasive wear conditions | |
| Gu et al. | Effects of Laser Scanning Rate and Ti Content on Wear of Novel Fe-Cr-B-Al-Ti Coating Prepared via Laser Cladding | |
| CN113862662B (en) | High-temperature self-hardening composite side guide plate lining plate and processing method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |