CN115301943A - Preparation method of mining wear-resistant impact-resistant long-life cutting tooth - Google Patents
Preparation method of mining wear-resistant impact-resistant long-life cutting tooth Download PDFInfo
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- CN115301943A CN115301943A CN202210859667.1A CN202210859667A CN115301943A CN 115301943 A CN115301943 A CN 115301943A CN 202210859667 A CN202210859667 A CN 202210859667A CN 115301943 A CN115301943 A CN 115301943A
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- 238000005520 cutting process Methods 0.000 title claims abstract description 65
- 238000005065 mining Methods 0.000 title claims abstract description 25
- 238000002360 preparation method Methods 0.000 title claims abstract description 22
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 59
- 239000000956 alloy Substances 0.000 claims abstract description 59
- 238000010438 heat treatment Methods 0.000 claims abstract description 21
- 238000000034 method Methods 0.000 claims abstract description 16
- 238000005219 brazing Methods 0.000 claims abstract description 11
- 239000000463 material Substances 0.000 claims abstract description 10
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 5
- 239000011265 semifinished product Substances 0.000 claims abstract description 5
- 239000010959 steel Substances 0.000 claims abstract description 5
- 238000004663 powder metallurgy Methods 0.000 claims abstract description 4
- 239000000843 powder Substances 0.000 claims description 123
- 239000002245 particle Substances 0.000 claims description 30
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 22
- 238000005245 sintering Methods 0.000 claims description 18
- 238000001238 wet grinding Methods 0.000 claims description 14
- 238000002156 mixing Methods 0.000 claims description 12
- 239000012188 paraffin wax Substances 0.000 claims description 11
- 238000003825 pressing Methods 0.000 claims description 11
- 239000007921 spray Substances 0.000 claims description 11
- 238000010791 quenching Methods 0.000 claims description 10
- 230000000171 quenching effect Effects 0.000 claims description 10
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 8
- 239000012299 nitrogen atmosphere Substances 0.000 claims description 8
- 239000011230 binding agent Substances 0.000 claims description 7
- 229910017263 Mo—C Inorganic materials 0.000 claims description 6
- 239000000047 product Substances 0.000 claims description 6
- 238000003466 welding Methods 0.000 claims description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims description 5
- 238000005496 tempering Methods 0.000 claims description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 4
- 229910052786 argon Inorganic materials 0.000 claims description 4
- 238000001816 cooling Methods 0.000 claims description 4
- 229910052802 copper Inorganic materials 0.000 claims description 4
- 239000010949 copper Substances 0.000 claims description 4
- 238000005485 electric heating Methods 0.000 claims description 4
- 239000000945 filler Substances 0.000 claims description 4
- 238000003754 machining Methods 0.000 claims description 4
- 229910052751 metal Inorganic materials 0.000 claims description 4
- 239000002184 metal Substances 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- 238000004321 preservation Methods 0.000 claims description 4
- 238000010583 slow cooling Methods 0.000 claims description 4
- 229920001030 Polyethylene Glycol 4000 Polymers 0.000 claims description 3
- 238000005238 degreasing Methods 0.000 claims description 3
- MTHSVFCYNBDYFN-UHFFFAOYSA-N diethylene glycol Chemical compound OCCOCCO MTHSVFCYNBDYFN-UHFFFAOYSA-N 0.000 claims description 3
- 238000005469 granulation Methods 0.000 claims description 3
- 230000003179 granulation Effects 0.000 claims description 3
- 239000011812 mixed powder Substances 0.000 claims description 3
- 238000005303 weighing Methods 0.000 claims 1
- 230000002035 prolonged effect Effects 0.000 abstract description 3
- UNASZPQZIFZUSI-UHFFFAOYSA-N methylidyneniobium Chemical compound [Nb]#C UNASZPQZIFZUSI-UHFFFAOYSA-N 0.000 description 17
- 230000035882 stress Effects 0.000 description 11
- 238000000498 ball milling Methods 0.000 description 8
- 239000011435 rock Substances 0.000 description 7
- 238000005728 strengthening Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 238000010008 shearing Methods 0.000 description 4
- 230000035939 shock Effects 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 3
- 230000005641 tunneling Effects 0.000 description 3
- 229910000851 Alloy steel Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 238000005299 abrasion Methods 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 239000003245 coal Substances 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000018109 developmental process Effects 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 230000036346 tooth eruption Effects 0.000 description 2
- 229910009043 WC-Co Inorganic materials 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000009412 basement excavation Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000011068 loading method Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000005121 nitriding Methods 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/12—Metallic powder containing non-metallic particles
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/60—Treatment of workpieces or articles after build-up
- B22F10/64—Treatment of workpieces or articles after build-up by thermal means
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
- B22F5/08—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of toothed articles, e.g. gear wheels; of cam discs
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K10/00—Welding or cutting by means of a plasma
- B23K10/02—Plasma welding
- B23K10/027—Welding for purposes other than joining, e.g. build-up welding
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/07—Alloys based on nickel or cobalt based on cobalt
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
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- Chemical & Material Sciences (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Physics & Mathematics (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
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Abstract
The invention relates to a preparation method of a mining wear-resistant impact-resistant long-life cutting pick. The invention relates to a preparation method of a mining wear-resistant impact-resistant long-life cutting pick, which comprises the following steps: s1: preparing high-entropy coarse-grain hard alloy teeth with the grain size of 4-6 microns, a binding phase of CoNiFeCrMo and a hard phase of WC and NbC by adopting a powder metallurgy method; s2: processing a stock blank by taking 42CrMo steel as a base material; s3: carrying out heat treatment on the storehouse body blank to obtain a storehouse body; s4: brazing the high-entropy coarse-grain hard alloy tooth obtained in the step S1 and the library obtained in the step S3 to obtain a cutting pick semi-finished product; s5: and (5) carrying out plasma surfacing on the semi-finished cutting tooth obtained in the step (S4), and surfacing a wear-resistant layer on the connecting surface of the hard alloy tooth and the warehouse body and the clamping ring at the bottom end of the warehouse body to obtain a finished cutting tooth. The cutting pick obtained by the preparation method of the mining wear-resistant impact-resistant long-life cutting pick has the advantages of wear resistance, stress impact resistance, high-temperature fatigue resistance and the like, and the service life of the cutting pick is greatly prolonged.
Description
Technical Field
The invention relates to the technical field of material preparation and mining, in particular to a mining wear-resistant impact-resistant long-life cutting pick.
Background
The cutting pick is a key stressed part for mine excavation and coal mining of the development machine, and the performance of the cutting pick directly determines the development efficiency and the production cost. The cutting pick is composed of a high-hardness and wear-resistant pick head (or alloy head) and a stress impact resistant library body. The mining cutting tooth has the advantages that the rock layer hardness is high, the geological condition is complex, the working condition is more severe compared with that of a coal cutting tooth, and the temperature can reach 700 ℃ at most when the mining cutting tooth is in friction with high-hardness rock, so that the mining cutting tooth is subjected to high-frequency high-stress impact in work and also subjected to long-time thermal fatigue and severe friction wear, the cutting tooth is easy to generate tooth head wear, tooth breakage and tooth falling in the use process, the high performance requirements are provided for an alloy head and a library body of the cutting tooth, the alloy head is required to be wear-resistant, high in toughness and thermal fatigue-resistant, and the library body is required to be high in toughness and impact resistance and high in connection strength with the alloy head.
At present, most alloy heads of cutting picks for mines are WC-Co hard alloy teeth. However, the hardness and toughness of the hard alloy are a pair of contradictions in the production of the hard alloy, the toughness can be improved by increasing the cobalt content or increasing the grain size, but the wear resistance is reduced, and the hardness and the toughness are difficult to be compatible, which is particularly obvious in mining cutting teeth. The storehouse body is the main atress part of pick, and it bears very big moment of torsion, bending and shearing force during operation, leads to the storehouse body to break very easily or fall the tooth, consequently, the good or bad of storehouse body performance has also seriously influenced the life of pick. In order to prevent the bank from breaking or falling off, the alloy steel used for the bank is usually subjected to heat treatment to increase the strength, and quenching or surface nitriding to increase the hardness to prevent the bank from falling off. However, the increase in hardness affects the toughness of the library body, and thus there is no effective measure for breaking or falling off of the library body.
Disclosure of Invention
Based on the method, the preparation method of the wear-resistant impact-resistant long-life cutting pick for the mine is provided, and the high toughness, wear resistance and thermal fatigue resistance of the alloy head of the cutting pick and the high toughness and high stress impact resistance of the library body are realized, so that the problems of too fast abrasion of the alloy head, tooth falling or tooth breaking when the cutting pick is used for tunneling a high-hardness and complex rock stratum are solved.
A preparation method of a mining wear-resistant impact-resistant long-life cutting pick comprises the following steps:
s1: preparing high-entropy coarse-grain hard alloy teeth with the grain size of 4-6 microns, a binding phase of CoNiFeCrMo and a hard phase of WC and NbC by adopting a powder metallurgy method;
s2: taking 42CrMo steel as a library body base material, and machining the base material into a library body structure to obtain a library body blank;
s3: carrying out heat treatment on the library body blank obtained in the step S2 to obtain a library body;
s4: brazing the high-entropy coarse-grain hard alloy tooth obtained in the step S1 and the library obtained in the step S3 to obtain a cutting tooth semi-finished product;
s5: and (5) carrying out plasma surfacing on the semi-finished cutting tooth obtained in the step (S4), and surfacing a wear-resistant layer on the connecting surface of the hard alloy tooth and the warehouse body and the clamping ring at the bottom end of the warehouse body to obtain a finished cutting tooth.
The grain size of cemented carbide also has a significant impact on wear resistance, toughness and thermal fatigue resistance. Under the same binding phase content, the coarser the crystal grain, the higher the toughness and the better the stress impact resistance of the alloy, and the better the thermal fatigue resistance, but the hardness is also reduced; the finer the crystal grain, the higher the hardness, but the lower the toughness and the high temperature fatigue resistance. The high-entropy coarse-grain hard alloy tooth of the cutting pick has the grain size of 4-6 mu m, and the large-grain structure can obviously improve the toughness and high-temperature wear resistance of the hard alloy tooth and realize the comprehensive properties of hardness, wear resistance, thermal shock resistance and fatigue
Meanwhile, coNiFeCrMo is used as a binding phase, so that the impact toughness and the high-temperature strength of the hard alloy tooth can be provided, the dependence on Co resources is reduced, and the added NbC can further improve the heat-conducting property of the alloy and enable the alloy to have high thermal shock resistance and thermal fatigue resistance, so that the hard alloy head has the advantages of wear resistance, stress shock resistance and thermal fatigue resistance, and the problem of too fast abrasion of cutting teeth in hard rock or complex rock stratum tunneling is solved.
In addition, the warehouse body is subjected to strengthening and toughening treatment, so that the high-strength and high-stress shearing and impact resistance of the warehouse body are realized, and the hard wear-resistant layer is overlaid on the joint surface of the cutting tooth and the warehouse body and the clamping ring at the bottom of the warehouse body, so that the hard wear-resistant layer can well play a role in protecting the warehouse body, the problem that the wear resistance of the warehouse body is reduced due to the strengthening and toughening treatment can be well solved, the wear resistance of key parts of the warehouse body is improved, the warehouse body is prevented from falling off, and the problems of tooth falling, breakage and the like of the cutting tooth are solved.
Overall, the cutting pick has the advantages of wear resistance, stress impact resistance, high temperature fatigue resistance and the like, and the service life of the cutting pick is greatly prolonged, so that the requirements of the heading machine in harsh working environments such as high hardness, complex geology and the like are well met.
Furthermore, in the binding phase CoNiFeCrMo in the step S1, the Co ratio is 40-60%, and the balance is Ni, fe, cr and Mo. The addition of Ni, fe, cr and Mo can improve the toughness and corrosion resistance of hard alloy, reduce the dependence on Co and lower cost, but their addition amount is too high, and can reduce strength, and when the content of binder phase is 40-60%, the comprehensive properties of strength and toughness of the alloy are good.
Further, in the hard phase in step S1, by mass fraction: 97 to 99 percent of WC; 1 to 3 percent of NbC. The alloy head has the working temperature of up to 700 ℃ when the cutting tooth works and very large thermal stress, and niobium carbide (NbC) is added, so that the alloy head has the advantages of improving the thermal conductivity and high-temperature hardness, being beneficial to improving the thermal conductivity of the hard alloy and improving the overall thermal shock resistance, thermal fatigue resistance and wear resistance of the alloy. However, too high a content of NbC causes a decrease in alloy strength, but too low a content of NbC causes insignificant strengthening effect.
Further, in the high-entropy coarse-grain cemented carbide in the step S1, by mass: 90 to 92 percent of hard phase; 8 to 10 percent of binder phase. The hardness is reduced and the high-temperature wear resistance is deteriorated due to the over-high content of the binding phase, so that the hard alloy teeth are worn too quickly; if the content of the binder phase is too low, the strength and toughness are reduced, and the teeth are likely to be broken during operation.
Further, the preparation method of the high-entropy coarse-grain cemented carbide tooth in the step S1 comprises the following steps:
a1: WC powder with the granularity of 25-35 mu m, nbC powder with the granularity of 0.8-2 mu m, co powder with the granularity of 1-3 mu m, ni powder, fe powder and Mo powder are respectively weighed according to the proportion and are uniformly mixed by a wet grinding and mixing method, wherein a medium used for wet grinding is ethanol, and paraffin or PEG4000 with the mass of 1.8-2.2% of the total mass of the powder is added;
a2: and C, performing spray granulation on the mixed powder obtained in the step A1, pressing the granulated powder into a blank tooth shape, and then performing degreasing sintering to obtain the hard alloy tooth.
For preparing 4-6 micron coarse-grain hard alloy, the needed WC powder granularity must be coarse, but if the WC powder is too coarse, the sintering activity is weakened, and the grain structure is easy to be uneven; but the WC powder is finer, so that the coarse-grain hard alloy with the grain size of more than 4 microns is difficult to prepare; nbC powder, co powder, ni powder, fe powder and Mo powder, wherein the finer the powder is, the more favorable the uniformity of components and structures are, but the cost of the powder raw material is increased; in addition, if the Co powder, the Ni powder, the Fe powder and the Mo powder are too fine, the powder is easy to oxidize, and the carbon control of the alloy is adversely affected.
Further, the sintering process conditions in the step A2 are as follows: the sintering temperature is 1490-1530 ℃, the temperature is preserved for 30-50 min under the vacuum condition, then the pressure is preserved for 10-30 min, and the pressure is preserved for 4-7 MPa.
Further, the heat treatment of the stock blank in the step S3 includes the following steps:
quenching: rapidly heating the warehouse body blank to 800-860 ℃ under the protection of nitrogen atmosphere, preserving the heat for 30-90 min, and then carrying out oil bath quenching;
tempering: and heating the quenched blank of the warehouse body to 420-500 ℃ under the protection of nitrogen atmosphere, preserving the heat for 30-90 min, and cooling the blank of the warehouse body to room temperature along with the furnace to obtain the warehouse body.
The 42CrMo alloy steel is subjected to heat treatment (also called strengthening and toughening treatment), the relative content of C, cr and Mo elements is adjusted, the quenching and tempering processes are performed, the hardness of the alloy is adjusted through the carbon content, the morphology and distribution of a hard phase are controlled, and the high-temperature strength of a tooth body is improved; the size, the number and the distribution of hard precipitated phases are controlled by adjusting quenching and tempering processes, so that the cutting tooth has very high strength, impact resistance and moderate hardness, high stress impact, shearing and fatigue stress loading of the mining cutting tooth are met, and the problem of tooth breakage is solved.
Further, the brazing in step S4 includes the steps of: heating the base body to 880-910 ℃ by adopting high-frequency electric heating, welding the high-entropy coarse-grain cemented carbide tooth and the base body into a whole by taking H62 copper or BCuZnMn as brazing filler metal, and performing heat preservation and slow cooling at 250-260 ℃ to obtain a semi-finished cutting tooth.
Furthermore, the wear-resistant layer in the step S5 is formed by plasma surfacing of Fe-Cr-V-Mo-C powder with the granularity of 50-150 mu m, and the thickness of the surfacing is 2-3 mm. Fe-Cr-V-Mo-C powder which has good intermiscibility with 42CrMo and strong metallurgical bonding is used as a raw material of a wear-resistant layer of a key component, and the Fe-Cr-V-Mo-C powder has very high bonding strength with a library body through plasma surfacing, the bonding strength with the library body exceeds 800MPa, the hardness of the wear-resistant layer reaches HRC61-64, and the problem of clamp ring falling is well solved. The granularity is too fine, the powder flowability is poor, and under-welding or surface defects are easy to occur in the surfacing process; the particle size is too coarse, the fluidity is enhanced, but the current for surfacing melting needs to be increased, and the surfacing is easy to form pores, so that the welding effect is influenced.
Furthermore, the current used for plasma surfacing is 90-110A, the powder feeding amount is 55-80 g/min, and the argon protection flow is 10-20L/min.
For a better understanding and practice, the present invention is described in detail below.
Detailed Description
The invention provides a preparation method of a mining wear-resistant impact-resistant long-life cutting pick, which comprises the following steps:
s1: preparing high-entropy coarse-grain hard alloy teeth with the grain size of 4-6 microns, a binding phase of CoNiFeCrMo and a hard phase of WC and NbC by adopting a powder metallurgy method;
s2: taking 42CrMo steel as a library body base material, and machining the base material into a library body structure to obtain a library body blank;
s3: carrying out heat treatment on the storehouse body blank obtained in the step S2 to obtain a storehouse body;
s4: brazing the high-entropy coarse-grain hard alloy tooth obtained in the step S1 and the library obtained in the step S2 to obtain a cutting pick semi-finished product;
s5: and (5) carrying out plasma surfacing on the semi-finished cutting tooth obtained in the step (S4), and surfacing a wear-resistant layer on the connecting surface of the hard alloy tooth and the warehouse body and the clamping ring at the bottom end of the warehouse body to obtain a finished cutting tooth.
Preferably: the binder phase CoNiFeCrMo contains Co in 40-60% and Ni, fe, cr and Mo in the balance. In the hard phase, the mass fraction: 97 to 99 percent of WC; 1 to 3 percent of NbC. In the high-entropy coarse-grain hard alloy, the mass fraction is as follows: 90 to 92 percent of hard phase; 8 to 10 percent of binder phase.
Preferably, the preparation method of the high-entropy coarse-grain cemented carbide tooth in the step S1 includes the following steps:
a1: WC powder with the granularity of 25-35 mu m, nbC powder with the granularity of 0.8-2 mu m, co powder with the granularity of 1-3 mu m, ni powder, fe powder and Mo powder are respectively weighed according to the proportion and are uniformly mixed by a wet grinding and mixing method, wherein a medium used for wet grinding is ethanol, and paraffin or PEG4000 with the mass of 1.8-2.2% of the total mass of the powder is added;
a2: and B, performing spray granulation on the mixed powder obtained in the step A1, pressing the granulated powder into a blank tooth shape, and then performing degreasing sintering to obtain the hard alloy tooth. The sintering process conditions are as follows: the sintering temperature is 1490-1530 ℃, the temperature is preserved for 30-50 min under the vacuum condition, then the pressure is preserved for 10-30 min, and the pressure is preserved for 4-7 MPa.
Preferably, the heat treatment of the stock blank in the step S3 includes the following steps:
quenching: rapidly heating the warehouse body to 800-860 ℃ under the protection of nitrogen atmosphere, preserving the heat for 30-90 min, and then carrying out oil bath quenching on the warehouse body blank;
tempering: and heating the quenched blank of the warehouse body to 420-500 ℃ under the protection of nitrogen atmosphere, preserving the heat for 30-90 min, and cooling the blank of the warehouse body to room temperature along with the furnace to obtain the warehouse body.
Preferably, the brazing in step S4 comprises the steps of: heating the library body to 880-910 ℃ by adopting high-frequency electric heating, welding the high-entropy coarse-grain cemented carbide tooth and the library body into a whole by taking H62 copper or BCuZnMn as brazing filler metal, and carrying out heat preservation and slow cooling at 250-260 ℃ to obtain a semi-finished cutting pick product.
Preferably, the wear-resistant layer in the step S5 is formed by plasma surfacing of Fe-Cr-V-Mo-C powder with the particle size of 50-150 microns, and the surfacing thickness is 2-3 mm. The current used for plasma surfacing is 90-110A, the powder feeding amount is 55-80 g/min, and the argon protection flow is 10-20L/min.
Example 1
87.3% by weight of WC powder having a particle size of 25 μm, 2.7% by weight of NbC powder having a particle size of 0.8 μm, 4% by weight of Co powder having a particle size of 1 μm, 2% by weight of Ni powder, 1% by weight of Fe powder, 1.5% by weight of Cr powder, and 1.5% by weight of Mo powder were weighed. Ethanol is used as a ball milling medium, paraffin with the mass being 2% of the total mass of the powder is added, and wet milling and uniform mixing are carried out. Spray granulating, and pressing the granulated powder into a blank tooth shape. Sintering at 1515 deg.C, maintaining the temperature under vacuum for 35min, and maintaining the pressure for 25min at 6MPa. The performance of the obtained high-entropy coarse-grain cemented carbide tooth was measured, and the results are shown in table 1.
Example 2
89.1% by weight of WC powder having a particle size of 25 μm, 0.9% by weight of NbC powder having a particle size of 0.8 μm, 6% by weight of Co powder having a particle size of 1 μm, 1% by weight of Ni powder, 1% by weight of Fe powder, 1% by weight of Cr powder, and 1% by weight of Mo powder were weighed. Ethanol is used as a ball milling medium, paraffin with the mass being 2% of the total mass of the powder is added, and wet milling and uniform mixing are carried out. Spray granulating, and pressing the granulated powder into a blank tooth shape. Sintering at 1490 deg.C, maintaining the temperature under vacuum for 50min, and maintaining the pressure for 10min at 5MPa. The performance of the obtained high-entropy coarse-grain cemented carbide tooth was measured, and the results are shown in table 1.
Example 3
89.24% by weight of WC powder having a particle size of 25 μm, 2.76% by weight of NbC powder having a particle size of 0.8 μm, 3.2% by weight of Co powder having a particle size of 1 μm, 1.6% by weight of Ni powder, 0.8% by weight of Fe powder, 1.2% by weight of Cr powder, and 1.2% by weight of Mo powder were weighed. Ethanol is used as a ball milling medium, paraffin with the mass being 2% of the total mass of the powder is added, and wet milling and uniform mixing are carried out. Spray granulating, and pressing the granulated powder into a blank tooth shape. Sintering at 1530 deg.C, maintaining the temperature for 40min under vacuum, and maintaining the pressure for 20min at 5MPa. The performance of the obtained high-entropy coarse-grain cemented carbide tooth was measured, and the results are shown in table 1.
Example 4
91.08% by weight of WC powder having a particle size of 25 μm, 0.92% by weight of NbC powder having a particle size of 0.8 μm, 4.8% by weight of Co powder having a particle size of 1 μm, 0.8% by weight of Ni powder, 0.8% by weight of Fe powder, 0.8% by weight of Cr powder, and 0.8% by weight of Mo powder were weighed. Ethanol is used as a ball milling medium, paraffin with the mass being 2% of the total mass of the powder is added, and wet milling and uniform mixing are carried out. Spray granulating, and pressing the granulated powder into a blank tooth shape. Sintering at 1510 deg.C, maintaining the temperature for 40min under vacuum, and maintaining the pressure for 20min at 4MPa. The performance of the obtained high-entropy coarse-grain hard alloy tooth is detected, and the result is shown in table 1.
Example 5
87.3% by weight of WC powder having a particle size of 35 μm, 2.7% by weight of NbC powder having a particle size of 2.0 μm, 4% by weight of Co powder having a particle size of 3 μm, 2% by weight of Ni powder, 1% by weight of Fe powder, 1.5% by weight of Cr powder and 1.5% by weight of Mo powder were weighed. Ethanol is used as a ball milling medium, paraffin with the mass being 2% of the total mass of the powder is added, and wet milling and uniform mixing are carried out. Spray granulating, and pressing the granulated powder into a blank tooth shape. Sintering at 1530 deg.C, maintaining the temperature under vacuum for 30min, and maintaining the pressure for 20min at 7MPa. The performance of the obtained high-entropy coarse-grain cemented carbide tooth was measured, and the results are shown in table 1.
Example 6
89.1% by weight of WC powder having a particle size of 35 μm, 0.9% by weight of NbC powder having a particle size of 2.0 μm, 6% by weight of Co powder having a particle size of 3 μm, 1% by weight of Ni powder, 1% by weight of Fe powder, 1% by weight of Cr powder, and 1% by weight of Mo powder were weighed. Ethanol is used as a ball milling medium, paraffin with the mass being 2% of the total mass of the powder is added, and wet milling and uniform mixing are carried out. Spray granulating, and pressing the granulated powder into a blank tooth shape. Sintering at 1510 deg.C, maintaining the temperature for 40min under vacuum, and maintaining the pressure for 20min at 4MPa. The performance of the obtained high-entropy coarse-grain cemented carbide tooth was measured, and the results are shown in table 1.
Example 7
89.24% by weight of WC powder having a particle size of 35 μm, 2.76% by weight of NbC powder having a particle size of 2.0 μm, 3.2% by weight of Co powder having a particle size of 3 μm, 1.6% by weight of Ni powder, 0.8% by weight of Fe powder, 1.2% by weight of Cr powder, and 1.2% by weight of Mo powder were weighed. Ethanol is used as a ball milling medium, paraffin with the mass being 2% of the total mass of the powder is added, and wet milling and uniform mixing are carried out. Spray granulating, and pressing the granulated powder into a blank tooth shape. Sintering at 1520 deg.C, maintaining the temperature under vacuum for 40min, and maintaining the pressure for 15min at 6MPa. The performance of the obtained high-entropy coarse-grain cemented carbide tooth was measured, and the results are shown in table 1.
Example 8
91.08% by weight of WC powder having a particle size of 35 μm, 0.92% by weight of NbC powder having a particle size of 2.0 μm, 4.8% by weight of Co powder having a particle size of 3 μm, 0.8% by weight of Ni powder, 0.8% by weight of Fe powder, 0.8% by weight of Cr powder, and 0.8% by weight of Mo powder were weighed out. Ethanol is used as a ball milling medium, paraffin with the mass being 2% of the total mass of the powder is added, and wet milling and uniform mixing are carried out. Spray granulating, and pressing the granulated powder into a blank tooth shape. Sintering at 1490 deg.C, maintaining the temperature under vacuum for 40min, and maintaining the pressure for 20min at 7MPa. The performance of the obtained high-entropy coarse-grain hard alloy tooth is detected, and the result is shown in table 1.
TABLE 1 high entropy coarse grain cemented carbide tooth mechanical properties
Example 9
(1) And (3) taking 42CrMo steel as a library body base material, and machining the library body base material into a library body structure to obtain a library body blank. Rapidly heating the warehouse body blank to 800-860 ℃ under the protection of nitrogen atmosphere, preserving the temperature for 30-90 min, and then carrying out oil bath quenching. And heating the quenched blank of the warehouse body to 420-500 ℃ under the protection of nitrogen atmosphere, preserving the heat for 30-90 min, and cooling the blank of the warehouse body to room temperature along with the furnace to obtain the warehouse body. The obtained library body is subjected to mechanical property detection and tensile strengthStrength of 1100MPa or more and impact power of 60J/cm or more 2 ， HRC≧35。
(2) And (2) heating the base body to 880-910 ℃ by adopting high-frequency electric heating, welding the high-entropy coarse-grain hard alloy tooth obtained in any one of the embodiments 1-8 and the base body obtained in the step (1) into a whole by taking H62 copper as brazing filler metal, and performing heat preservation and slow cooling at 250-260 ℃ to obtain a cutting tooth semi-finished product.
(3) And (3) carrying out plasma surfacing on the connecting surface of the high-entropy hard alloy tooth and the library body of the semi-finished cutting pick product obtained in the step (2) and the clamping ring at the bottom end of the library body by using Fe-Cr-V-Mo-C powder with the particle size of 70-120 mu m to form a wear-resistant layer with the thickness of 2-3 mm, so as to obtain the finished cutting pick product. The current used for plasma surfacing is 90-110A, the powder feeding amount is 55-80 g/min, and the argon protection flow is 10-20L/min. The performance of the wear-resistant layer is detected, the bonding strength is more than or equal to 800MPa, and the hardness is more than or equal to 61 HRC.
The grain size of the high-entropy coarse-grain hard alloy tooth of the cutting pick reaches 4-6 mu m, the bending strength is more than or equal to 2400MPa, and the HRA is more than or equal to 86, so that the large grain size can keep high strength and hardness, and the high-entropy coarse-grain hard alloy tooth is very helpful for improving the wear resistance, stress resistance and thermal fatigue resistance of the hard alloy tooth under the high-temperature condition; meanwhile, the hard alloy tooth adopts CoNiFeCrNb as a binding phase, and the high-entropy effect can improve the impact toughness and high-temperature strength of the hard alloy tooth and reduce the dependence on Co resources, so that the hard alloy head has the advantages of wear resistance, stress impact resistance and thermal fatigue resistance, and the problem that the cutting tooth fails due to the fact that the hard alloy tooth is worn too fast in the tunneling process of hard rock or complex rock stratum is solved. Secondly, the invention carries out strengthening and toughening treatment on the storehouse body, realizes high strength and high stress shearing and impact resistance of the storehouse body, and further improves the connection performance of the storehouse body and the hard alloy tooth on one hand, improves the wear resistance of key parts of the storehouse body on the other hand, prevents the storehouse body from falling off, and solves the problems of tooth falling and breakage of the cutting tooth and the like by overlaying the hard wear-resistant layer with strong metallurgical bonding on the connection surface of the cutting tooth and the storehouse body and the snap ring at the bottom of the storehouse body. Overall, the cutting pick has the advantages of wear resistance, stress impact resistance, high temperature fatigue resistance and the like, and the service life of the cutting pick is greatly prolonged, so that the requirements of the heading machine in harsh working environments such as high hardness, complex geology and the like are well met.
The above-mentioned embodiments only express several embodiments of the present invention, and the description thereof is specific and detailed, but not to be understood as limiting the scope of the invention. It should be noted that numerous changes and modifications can be made by those skilled in the art without departing from the inventive concepts and it is intended that such changes and modifications be covered by the present invention.
Claims (10)
1. The preparation method of the mining wear-resistant impact-resistant long-life cutting pick is characterized by comprising the following steps:
s1: preparing high-entropy coarse-grain hard alloy teeth with the grain size of 4-6 microns, a binding phase of CoNiFeCrMo and a hard phase of WC and NbC by adopting a powder metallurgy method;
s2: taking 42CrMo steel as a library body base material, and machining the base material into a library body structure to obtain a library body blank;
s3: carrying out heat treatment on the storehouse body blank obtained in the step S2 to obtain a storehouse body;
s4: brazing the high-entropy coarse-grain hard alloy tooth obtained in the step S1 and the library obtained in the step S3 to obtain a cutting pick semi-finished product;
s5: and D, performing plasma surfacing on the semi-finished cutting pick product obtained in the step S4, and surfacing a wear-resistant layer on the joint surface of the hard alloy tooth and the storehouse body and the clamping ring at the bottom end of the storehouse body to obtain a finished cutting pick product.
2. The preparation method of the mining wear-resistant impact-resistant long-life cutting pick according to claim 1, characterized in that: in the step S1, the binder phase CoNiFeCrMo contains 40-60% of Co and the balance of Ni, fe, cr and Mo.
3. The preparation method of the mining wear-resistant impact-resistant long-life cutting pick according to claim 1, characterized in that: in the hard phase in the step S1, the mass fraction:
WC 97～99％；
NbC 1～3％。
4. the preparation method of the mining wear-resistant impact-resistant long-life cutting pick according to claim 1, characterized in that: in the high-entropy coarse-grain hard alloy in the step S1, the mass fraction is as follows:
90 to 92 percent of hard phase;
8 to 10 percent of binder phase.
5. The preparation method of the mining wear-resistant impact-resistant long-life cutting pick according to claim 1, characterized in that: the preparation method of the high-entropy coarse-grain hard alloy tooth in the step S1 comprises the following steps:
a1: weighing WC powder with the particle size of 25-35 mu m, nbC powder with the particle size of 0.8-2 mu m, co powder with the particle size of 1-3 mu m, ni powder, fe powder and Mo powder respectively according to a proportion, and uniformly mixing the powder by a wet grinding and mixing method, wherein a medium used for wet grinding is ethanol, and paraffin or PEG4000 with the mass accounting for 1.8-2.2% of the total mass of the powder is added;
a2: and C, performing spray granulation on the mixed powder obtained in the step A1, pressing the granulated powder into a blank tooth shape, and then performing degreasing sintering to obtain the hard alloy tooth.
6. The preparation method of the mining wear-resistant impact-resistant long-life cutting pick according to claim 5, characterized in that: the sintering process conditions in the step A2 are as follows: the sintering temperature is 1490-1530 ℃, the temperature is preserved for 30-50 min under the vacuum condition, then the pressure is maintained for 10-30 min, and the pressure is maintained for 4-7 MPa.
7. The preparation method of the mining wear-resistant impact-resistant long-life cutting pick according to claim 1, characterized in that: the heat treatment of the storehouse body blank in the step S3 comprises the following steps:
quenching: rapidly heating the warehouse body to 800-860 ℃ under the protection of nitrogen atmosphere, preserving the heat for 30-90 min, and then carrying out oil bath quenching on the warehouse body blank;
tempering: and (3) heating the quenched storehouse body blank to 420-500 ℃ under the protection of nitrogen atmosphere, preserving the heat for 30-90 min, and cooling the blank to room temperature along with the furnace to obtain the storehouse body.
8. The preparation method of the mining wear-resistant impact-resistant long-life cutting pick according to claim 1, characterized in that: the brazing in step S4 includes the steps of: heating the library body to 880-910 ℃ by adopting high-frequency electric heating, welding the high-entropy coarse-grain cemented carbide tooth and the library body into a whole by taking H62 copper or BCuZnMn as brazing filler metal, and carrying out heat preservation and slow cooling at 250-260 ℃ to obtain a semi-finished cutting pick product.
9. The preparation method of the mining wear-resistant impact-resistant long-life cutting pick according to claim 1, characterized in that: in the step S5, the wear-resistant layer is formed by plasma surfacing of Fe-Cr-V-Mo-C powder with the granularity of 50-150 mu m, and the surfacing thickness is 2-3 mm.
10. The preparation method of the mining wear-resistant impact-resistant long-life cutting pick according to claim 9, characterized in that: the current used for plasma surfacing is 90-110A, the powder feeding amount is 55-80 g/min, and the argon protection flow is 10-20L/min.
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