CN117512379A - Steel base-metal carbon/nitride steel bonded hard alloy and preparation method thereof - Google Patents
Steel base-metal carbon/nitride steel bonded hard alloy and preparation method thereof Download PDFInfo
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- CN117512379A CN117512379A CN202311480803.7A CN202311480803A CN117512379A CN 117512379 A CN117512379 A CN 117512379A CN 202311480803 A CN202311480803 A CN 202311480803A CN 117512379 A CN117512379 A CN 117512379A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 126
- 239000010959 steel Substances 0.000 title claims abstract description 126
- 239000000956 alloy Substances 0.000 title claims abstract description 66
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 62
- 150000004767 nitrides Chemical class 0.000 title claims abstract description 41
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 title claims abstract description 25
- 229910052799 carbon Inorganic materials 0.000 title claims abstract description 23
- 239000010953 base metal Substances 0.000 title claims abstract description 10
- 238000002360 preparation method Methods 0.000 title abstract description 12
- 239000000843 powder Substances 0.000 claims abstract description 158
- 229910052751 metal Inorganic materials 0.000 claims abstract description 54
- 239000002184 metal Substances 0.000 claims abstract description 54
- 239000002131 composite material Substances 0.000 claims abstract description 48
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims abstract description 41
- 238000000034 method Methods 0.000 claims abstract description 40
- 238000000498 ball milling Methods 0.000 claims abstract description 38
- 238000011068 loading method Methods 0.000 claims abstract description 16
- 238000002156 mixing Methods 0.000 claims abstract description 7
- 238000005245 sintering Methods 0.000 claims description 76
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical group C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 claims description 53
- 229910001311 M2 high speed steel Inorganic materials 0.000 claims description 25
- 239000010935 stainless steel Substances 0.000 claims description 17
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- 238000004519 manufacturing process Methods 0.000 claims description 12
- 238000000280 densification Methods 0.000 claims description 10
- 239000011159 matrix material Substances 0.000 claims description 9
- 229910000997 High-speed steel Inorganic materials 0.000 claims description 6
- 238000006243 chemical reaction Methods 0.000 claims description 6
- 229910000617 Mangalloy Inorganic materials 0.000 claims description 5
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 claims description 4
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 claims description 4
- 229910000975 Carbon steel Inorganic materials 0.000 claims description 3
- 229910001315 Tool steel Inorganic materials 0.000 claims description 3
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- 238000005520 cutting process Methods 0.000 claims description 3
- 239000011812 mixed powder Substances 0.000 claims description 3
- MZLGASXMSKOWSE-UHFFFAOYSA-N tantalum nitride Chemical compound [Ta]#N MZLGASXMSKOWSE-UHFFFAOYSA-N 0.000 claims description 3
- NFFIWVVINABMKP-UHFFFAOYSA-N methylidynetantalum Chemical compound [Ta]#C NFFIWVVINABMKP-UHFFFAOYSA-N 0.000 claims description 2
- 229910003468 tantalcarbide Inorganic materials 0.000 claims description 2
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- BPJYAXCTOHRFDQ-UHFFFAOYSA-L tetracopper;2,4,6-trioxido-1,3,5,2,4,6-trioxatriarsinane;diacetate Chemical compound [Cu+2].[Cu+2].[Cu+2].[Cu+2].CC([O-])=O.CC([O-])=O.[O-][As]1O[As]([O-])O[As]([O-])O1.[O-][As]1O[As]([O-])O[As]([O-])O1 BPJYAXCTOHRFDQ-UHFFFAOYSA-L 0.000 description 6
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- WRIDQFICGBMAFQ-UHFFFAOYSA-N (E)-8-Octadecenoic acid Natural products CCCCCCCCCC=CCCCCCCC(O)=O WRIDQFICGBMAFQ-UHFFFAOYSA-N 0.000 description 1
- LQJBNNIYVWPHFW-UHFFFAOYSA-N 20:1omega9c fatty acid Natural products CCCCCCCCCCC=CCCCCCCCC(O)=O LQJBNNIYVWPHFW-UHFFFAOYSA-N 0.000 description 1
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- JLTDJTHDQAWBAV-UHFFFAOYSA-N N,N-dimethylaniline Chemical compound CN(C)C1=CC=CC=C1 JLTDJTHDQAWBAV-UHFFFAOYSA-N 0.000 description 1
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- ZQPPMHVWECSIRJ-UHFFFAOYSA-N Oleic acid Natural products CCCCCCCCC=CCCCCCCCC(O)=O ZQPPMHVWECSIRJ-UHFFFAOYSA-N 0.000 description 1
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- 239000010941 cobalt Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
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- 238000005261 decarburization Methods 0.000 description 1
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- QXJSBBXBKPUZAA-UHFFFAOYSA-N isooleic acid Natural products CCCCCCCC=CCCCCCCCCC(O)=O QXJSBBXBKPUZAA-UHFFFAOYSA-N 0.000 description 1
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- 238000001000 micrograph Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 239000000178 monomer Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- ZQPPMHVWECSIRJ-KTKRTIGZSA-N oleic acid Chemical compound CCCCCCCC\C=C/CCCCCCCC(O)=O ZQPPMHVWECSIRJ-KTKRTIGZSA-N 0.000 description 1
- 230000005501 phase interface Effects 0.000 description 1
- 229920001343 polytetrafluoroethylene Polymers 0.000 description 1
- 239000004810 polytetrafluoroethylene Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
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- 230000001681 protective effect Effects 0.000 description 1
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- 230000000171 quenching effect Effects 0.000 description 1
- 239000004576 sand Substances 0.000 description 1
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- 239000002436 steel type Substances 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 238000003786 synthesis reaction Methods 0.000 description 1
- 230000002194 synthesizing effect Effects 0.000 description 1
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- BFKJFAAPBSQJPD-UHFFFAOYSA-N tetrafluoroethene Chemical group FC(F)=C(F)F BFKJFAAPBSQJPD-UHFFFAOYSA-N 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 238000009827 uniform distribution Methods 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
-
- 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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
-
- 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
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
- C22C1/051—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor
-
- 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
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
- B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Optics & Photonics (AREA)
- Manufacturing & Machinery (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention relates to a steel base-metal carbon/nitride steel bonded hard alloy and a preparation method thereof, wherein the method comprises the following steps: ball milling is carried out on the steel-based powder and the metal carbo/nitride powder to obtain uniform composite powder; loading composite powder into an alumina tube and applying a range of pulse currents of pressure and current density to the green composite powder by upper and lower ram electrodes; after a set time, the pulse current is disconnected to quickly cool the block formed by the green body, and the steel base-metal carbon/nitride steel bonded hard alloy block is obtained. The invention adopts two mature commercial powders as raw materials for illustration, realizes the uniform mixing of main components by ball milling in a short time, solves the problem of complicated regulation and control of powder components in other steel bonded hard alloy powder metallurgy technologies, simultaneously avoids the problem of introducing impurities into the steel bonded hard alloy materials by the ball milling process without adding a regulating agent, and highlights the characteristics of high efficiency and cleanness of the invention.
Description
Technical Field
The invention belongs to the technical field of powder metallurgy, and particularly relates to a steel base-metal carbon/nitride steel bonded hard alloy and a preparation method thereof.
Background
With the development of industrial technology and the expansion of production scale, the demand for high-performance wear-resistant materials is increasing. The traditional tungsten-cobalt hard alloy has excellent wear resistance, but the characteristics of high density and poor processability limit the application scene of the tungsten-cobalt hard alloy, and tungsten and cobalt resources of China are relatively deficient, so that development of a high-performance wear-resistant material with abundant and relatively low-cost main components is needed.
The steel bonded hard alloy is a metal-ceramic composite material, steel is used as a bonding phase, and a hard compound is used as a hard phase, so that the steel bonded hard alloy has the characteristics of low production cost, low density, good machining performance and the like. Titanium carbide has the characteristics of high hardness, high elastic modulus, high thermal stability and the like, and has good wettability with a steel matrix. In addition, the solubility of titanium carbide in Fe solution is low, so that the grain size of titanium carbide grains grows slightly due to the elution effect in the sintering process, and titanium carbide is considered to be an ideal material for preparing steel-bonded hard alloy. According to different service conditions, the bonding phase for preparing the steel bonded hard alloy can be selected from different steel types, such as stainless steel, high manganese steel, corrosion-resistant steel and the like. The M2 high-speed steel has the performance between W-system and Mo-system high-speed steel, excellent thermal performance and toughness, low decarburization sensitivity and overheat sensitivity and good comprehensive performance. The main preparation process of the existing steel bonded hard alloy comprises the following steps: casting, high temperature self-propagating synthesis, impregnation, powder metallurgy, and the like. The casting method is a technology in which the hard phase is directly added into molten steel, and the uniform distribution of hard phase particles in the base phase is realized through stirring, ultrasonic vibration and other technologies. The raw materials for preparing the steel bonded hard alloy by the casting method are required to be liquid binding phase and hard phase which have good wettability and relatively close density, and meanwhile, the production process is required to be carried out under the condition of relatively high temperature, so the casting method has high requirements on the raw materials and equipment. The high temperature self-propagating synthesis method is to ignite the hard phase principle in certain environment to produce exothermic reaction and to initiate the reaction of the surrounding material until all the material in the system is reacted completely. The interface bonding formed by the hard phase and the bonding phase of the steel bonded hard alloy prepared by the high-temperature self-propagating synthesis method is stronger than other interface bonding, but the product has more pores, low density and low strength and cannot be used as a structural member.
In the first prior art, organic monomers of methyl hydroxy ethyl ester, toluene and tetrafluoroethylene are firstly prepared into a premix, then Ti powder, graphite powder, steel-based alloy powder, oleic acid, benzoyl peroxide and dimethylaniline are added into the mixture according to a certain mass ratio to form metal slurry, and then the metal slurry is added into 3D printing equipment to be layered and printed into a required structure, and then the structure is dried in a vacuum environment and degummed in a protective atmosphere to obtain a green body. Sintering the green body in a vacuum environment at 1100-1300 ℃ for 2-4 hours, thermally decomposing polytetrafluoroethylene in the sintering process, synthesizing hard phase titanium carbide in situ in the steel-based green body, promoting activated sintering, and finally obtaining the titanium carbide and the steel-bonded hard alloy. The powder preparation process of the method is complex, the sintering time is long, and the finally obtained block material has low density and cannot be used as a structural material.
In the second prior art, tungsten powder, steel powder, graphite powder, niobium powder or tantalum powder are uniformly mixed according to a certain proportion, and the mixed powder is filled at the bottom of a mould provided with a refractory metal microscope until the powder covers the metal microscope. And then continuously preparing a mixed layer of metal fibers and composite powder above the mixed layer, wherein the metal microscopes of the same layer are parallel to each other, and the metal microscopes of adjacent mixed layers are different in arrangement direction. And compacting the composite preform into a pressed compact by using a cold isostatic press, and putting the pressed compact into a sintering furnace to sequentially complete dewaxing, sintering, quenching and tempering according to a temperature gradient, thereby finally obtaining the steel bonded hard alloy block. The method has the advantages of complex powder blank making process, long sintering process time and high temperature, and severely limits the production efficiency.
Aiming at a plurality of problems of the steel bonded hard alloy prepared by the traditional process, including low density, low hard phase content, low hardness strength, poor wear resistance, long preparation time and the like. Therefore, there is a need to study a steel-based-metal carbon/nitride steel cemented carbide and a method of preparing the same.
Disclosure of Invention
In order to overcome the above problems in the prior art, the present invention provides a steel-based-metal carbon/nitride steel bonded cemented carbide and a method for preparing the same, which are used for solving the above problems in the prior art.
A method of making a steel-based-metal carbon/nitride steel bonded cemented carbide, the method comprising the steps of:
s1, mixing and ball milling steel-based powder and metal carbo/nitride to obtain uniformly mixed composite powder;
s2, loading the uniformly mixed composite powder into an alumina tube, and applying pulse current with certain pressure and current density to the composite powder through an upper pressure head electrode and a lower pressure head electrode to finish the rapid densification and interface reaction process;
s3, after a set time, cutting off pulse current to enable the block obtained by sintering the composite powder to be cooled rapidly, and obtaining the steel base-metal carbon/nitride steel bonded hard alloy block.
In aspects and any one of the possible implementations described above, there is further provided an implementation in which the steel base is M2 high speed steel or other brands of high speed steel, high manganese steel, stainless steel, heat resistant steel, tool steel or carbon steel powder.
In aspects and any one of the possible implementations described above, there is further provided an implementation in which the metal carbon/nitride is titanium carbide, titanium nitride, tungsten carbide, tantalum carbide, or tantalum nitride powder.
In the aspect and any possible implementation manner as described above, there is further provided an implementation manner, where the S1 specifically includes: mixing steel-based powder with a certain mass and metal/nitride powder with a certain mass according to a certain mass ratio, and carrying out dry vacuum ball milling to obtain the composite powder, wherein the mass fraction of the steel-based powder in the composite powder is 5-95 wt%, and the mass fraction of the metal carbon/nitride powder is 5-95 wt%.
Aspects and any one of the possible implementations as described above, further providing an implementation, the range of pressuresAnd current densities are respectively: the pressure is 50-550 MPa, and the current density is 1.2-5.2X10 6 A/m 2 The electric field strength is 500-3500V/m.
In aspects and any possible implementation manner as described above, there is further provided an implementation manner, where the set time is 10-120 seconds.
In aspects and any one of the possible implementations described above, there is further provided an implementation in which the pressure is 500MPa and the current density of the pulse current is 4.8x10 6 A/m 2 The electric field strength was 1000V/m.
In the aspect and any possible implementation manner described above, there is further provided an implementation manner, where the metal carbo/nitride is titanium carbide, and the mass fraction of the titanium carbide powder in the mixed powder is 10wt%, 20wt%, 30wt%, 40wt%, 50wt%, 60wt%, or 70wt%.
The invention also provides a steel base-metal carbon/nitride steel bonded hard alloy, which is prepared by adopting the method.
In the aspects and any possible implementation manner, there is further provided an implementation manner, wherein the relative density of the steel bonded hard alloy block is equal to or greater than 99.5%, the vickers hardness is 200-2000 Hv, and the compressive strength is 400-4500 MPa.
The beneficial effects of the invention are that
Compared with the prior art, the invention has the following beneficial effects:
the method for preparing the steel base-metal carbon/nitride steel bonded hard alloy comprises the following steps: ball milling is carried out on the steel-based powder and the metal carbo/nitride powder to obtain uniform composite powder; loading composite powder into an alumina tube and applying a range of pulse currents of pressure and current density to the green composite powder by upper and lower ram electrodes; after a set time, the pulse current is disconnected to quickly cool the block formed by the green body, and the steel base-metal carbon/nitride steel bonded hard alloy block is obtained. Compared with the existing steel bonded hard alloy preparation technology, the invention has the following remarkable advantages:
(1) The invention adopts two mature commercial powders as raw materials, realizes the uniform mixing of main components through short-time ball milling, solves the problem of complicated powder component regulation of other steel bonded hard alloy powder metallurgy technologies, simultaneously avoids the problem of introducing impurities into the steel bonded hard alloy materials through the ball milling process without adding a regulating agent, and highlights the characteristics of high efficiency and cleanness.
(2) The invention realizes the preparation of the novel steel bonded hard alloy with complete compactness and uniform components in a short time, such as 30 seconds, by utilizing the flash sintering technology. Compared with the existing steel bonded hard alloy preparation process, the sintering time and energy consumption of the invention are greatly reduced, and the green energy-saving characteristic of the invention is highlighted.
(3) The invention prepares the fully compact high-performance M2 high-speed steel-titanium carbide steel bonded hard alloy materials with different hard phase contents through flash sintering, and solves the problems of low hard phase content, low density, component segregation and poor strength of the high-titanium carbide hard phase steel bonded hard alloy prepared by the prior art. The mass fraction of titanium carbide in the M2 high-speed steel-titanium carbide hard alloy system prepared by the method is 0-95 wt%, and the steel bonded hard alloy products in the range can be completely compact and have uniform components, so that the characteristic of strong raw material adaptability of the invention is highlighted.
Drawings
FIG. 1 is a graph showing the variation of the Vickers hardness of steel-bonded hard paper alloys of different hard phase mass fractions of fully dense titanium carbide according to the present invention.
FIG. 2 is a scanning electron microscope image of an 80% wtM2 high speed steel-20% titanium carbide steel bonded cemented carbide prepared according to the present invention.
FIG. 3 is a graph showing the relationship between the increase in sintering time and the densification of a cemented carbide of a titanium carbide steel for producing a high speed steel of 60% wtM2 to 40% by weight in accordance with the present invention.
FIG. 4 is a graph of 40% wtM2 high speed steel-60% titanium carbide cemented carbide at 4.5X10 6 A/m 2 And sintering under the conditions of current density and 500MPa pressure, and changing the temperature after switching off the pulse power supply.
FIG. 5 is a compressive stress strain curve for a 10% wtM2 high speed steel-90% by weight titanium carbide steel cemented carbide;
FIG. 6 is a flow chart of the preparation of the present invention.
Detailed Description
For a better understanding of the present invention, the present disclosure includes, but is not limited to, the following detailed description, and similar techniques and methods should be considered as falling within the scope of the present protection. In order to make the technical problems, technical solutions and advantages to be solved more apparent, the following detailed description will be given with reference to the accompanying drawings and specific embodiments.
It should be understood that the described embodiments of the invention are only some, but not all, embodiments of the invention. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention.
The terminology used in the embodiments of the invention is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention. As used in this application and the appended claims, the singular forms "a," "an," and "the" are intended to include the plural forms as well, unless the context clearly indicates otherwise.
In order to solve the problems of low density, low hard phase content, low hardness strength, poor wear resistance, long production time and the like of the steel bonded hard alloy prepared by the traditional process, as shown in fig. 6, the invention provides a method for preparing the steel-based-metal carbo/nitride steel bonded hard alloy, which comprises the following steps:
s1: mixing and ball milling the steel-based powder and the metal carbo/nitride to obtain uniformly mixed composite powder
S2: loading the uniformly mixed composite powder into an alumina tube, applying pulse current with certain pressure and current density to the composite powder through an upper pressure head electrode and a lower pressure head electrode, rapidly liquefying a steel-based bonding phase under the action of Joule heat, rapidly filling gaps between metal carbo/nitrides by the bonding phase under the action of pressure, and completing rapid densification and interface reaction processes;
s3: after a set time, the pulse current is disconnected to quickly cool the block obtained by sintering the composite powder, and the steel-based binding phase and the metal carbo/nitride are subjected to interface reaction or second phase in-situ precipitation to obtain the steel-based-metal carbo/nitride steel bonded hard alloy block with good combination of the matrix and the reinforced phase interface.
Preferably, the steel-based powder having various particle sizes and particle shapes and the metal carbo/nitride powder having various particle sizes and particle shapes having 0 to 95wt% are mixed in a certain mass ratio and dry vacuum ball-milled, the particle sizes and particle shapes of which are not limited in the present invention.
Preferably, the steel-based powder belongs to a binding phase, and comprises M2 high-speed steel with various grain sizes and grain shapes and other high-speed steel with different brands or models, high-manganese steel, stainless steel, heat-resistant steel, tool steel, carbon steel and other steel-based powder, and the selected hard phase comprises titanium carbide, titanium nitride, tungsten carbide, tantalum nitride and other hard phase powder with various grain sizes and grain shapes, and the grain sizes and the grain shapes are not limited by the invention.
Preferably, the alumina tube is part of a sintering assembly comprising a cylindrical metal mold, an insulating alumina tube, upper and lower refractory metal indenter electrodes disposed in the insulating alumina tube and spaced apart by a distance space in which a homogeneous composite powder to be sintered is received.
Preferably, the pressure of 50 to 550MPa and the pressure of 1.2 to 5.2X10 are simultaneously applied to the insulated alumina tube of the sintering unit in S2 by using a hydraulic device and a pulse power source which are insulated from each other 6 A/m 2 A direct current pulse of current density. The temperature of the steel-based metal carbon/nitride composite powder is rapidly increased under the action of pressure and pulse, and the steel-based powder is rapidly converted into a bonding liquid phase to fill the pores among metal carbon/nitride powder particles. Meanwhile, under the action of pressure and pulse current, the electron migration rate and diffusion rate of the interface between the steel base phase and the metal carbon/nitride are greatly improved, and strong interface bonding is formed in extremely short time, so that a fully compact high-performance steel bonded hard alloy block is finally obtained.
According to the invention, M2 high-speed steel and titanium carbide are used as composite powder, a flash sintering technology is utilized to obtain the M2-titanium carbide steel bonded hard alloy material, and the M2-titanium carbide steel bonded hard alloy prepared in less than 30 seconds has the advantages of high hard phase content, high density, high uniformity, high strength and hardness and short sintering time. The method of the invention is not limited to two main components of M2 high-speed steel and titanium carbide, and is also applicable to steel-based powder such as high-speed steel, stainless steel, high manganese steel, high carbon high chromium steel and the like with the brand, grain size and grain shape, and hard equivalent metal carbo/nitrides such as tungsten carbide, titanium nitride and the like.
Taking the preparation of M2 high-speed steel-titanium carbide steel bonded hard alloy as an example, firstly ball milling is carried out on M2 high-speed steel powder and titanium carbide powder, and the specific steps are as follows: the method comprises the steps of loading micron-sized nearly spherical M2 high-speed steel powder and micron-sized titanium carbide powder into a ball milling tank according to a certain mass ratio, and then adding stainless steel grinding balls with the mass 500 times of the whole powder into the ball milling tank. The ball milling pot was sealed and evacuated to a vacuum of about 10 3 Pa, then placing the powder into a planetary ball mill to perform dry ball milling according to the set ball milling time and ball milling speed, and finally obtaining the uniformly mixed M2 high-speed steel-titanium carbide composite powder. The method comprises the steps of loading an insulating alumina tube into a core of a cylindrical metal mold with the same height, loading a refractory metal cylinder at the bottom of the alumina tube as a lower pressure head electrode, loading M2 high-speed steel-titanium carbide composite powder into the alumina tube, loading another refractory metal cylinder at the upper part of the powder as an upper pressure head electrode, and forming a complete flash sintering assembly by combining the M2 high-speed steel-titanium carbide powder green compact, the alumina tube, the upper pressure head electrode, the lower pressure head electrode and the metal mold.
The hydraulic device and the pulse power supply apply high-pressure and high-current-density pulse current to the M2 high-speed steel-titanium carbide powder green compact in the flash sintering assembly through the upper pressure head electrode and the lower pressure head electrode respectively, under the condition, the temperature of the composite powder green compact is rapidly increased, the M2 high-speed steel phase in the green compact rapidly generates bonding liquid phase flow, the pores among refractory titanium carbide powder particles are filled, and meanwhile, under the action of pressure and pulse current, the electron migration rate and the diffusion rate of an interface between a steel base phase and metal carbon/nitride are greatly improved, so that strong interface combination is formed in extremely short time, and finally, the fully compact high-performance steel bonded hard alloy block is obtained. After a period of time, the pulse power supply is disconnected, the pressure of the hydraulic device is removed, and the generated block is taken out from the sintering assembly, and the block is the M2 high-speed steel-titanium carbide steel bonded hard alloy which is completely compact and has uniform components. According to the invention, M2 high-speed steel is selected as a binding phase, titanium carbide is selected as a hard phase, and a fully dense M2 high-speed steel-titanium carbide high-performance hard alloy with uniformly distributed components is developed through a flash sintering technology.
The following is another specific embodiment, specifically: a method for developing a novel steel bonded carbide of M2 high speed steel-titanium carbide by flash sintering technology, comprising the steps of:
(1) And (3) placing the micron-sized nearly spherical M2 high-speed steel powder and the micron-sized titanium carbide powder into a ball milling tank according to a certain mass ratio. Stainless steel milling balls 5 times the total mass of the composite powder were then added to the milling jar and the jar was sealed. Vacuum pump was used to reduce the vacuum level inside the ball milling tank to about 10 3 Pa, and then loading into a planetary ball mill;
(2) The ball milling process was a dry ball mill with a rotational speed of 300rpm for 1 hour. After ball milling is finished, pouring the powder in the tank and the grinding balls into a sample separating sieve for sieving to obtain fine-particle mixed M2 high-speed steel-titanium carbide composite powder;
(3) The method comprises the steps of loading an insulating alumina tube with equal height into a metal cylindrical die core, loading a refractory metal cylinder at the bottom of the alumina tube as a lower pressure head electrode, loading 5-6 g of M2 high-speed steel-titanium carbide composite powder into the alumina tube, loading another refractory metal cylinder at the upper part of the powder as an upper pressure head electrode, and forming a powder green compact, the alumina tube, the upper pressure head electrode, the lower pressure head electrode and the metal die together to form a complete flash sintering assembly. The hydraulic device and the pulse power supply respectively apply pressure of 50-500 MPa and 1.2-5.2X10 to the flash sintering assembly through the upper pressure head electrode and the lower pressure head electrode 6 A/m 2 Pulse current with current density and electric field with electric field strength of 500-3500V/M, M2 high-speed steel powder particles rapidly generate liquid phase under the condition of extremely high temperature rising rate, and rapidly flow and fill titanium carbide under the action of pressurePores between the particles and form strong interface bonding with the titanium carbide particles.
(4) And (3) after the pulse current is processed for about 30 seconds, the power supply is turned off, the pressure of the hydraulic device is removed, and the flash sintering assembly is taken down and disassembled to obtain the M2 high-speed steel-titanium carbide novel steel bonded hard alloy with uniform and complete compact components.
The following are specific examples
Example 1
In the embodiment, 0-90 wt% of micron-sized near-spherical M2 high-speed steel powder and 0-90 wt% of micron-sized titanium carbide are taken as raw material powder. The two powders are weighed according to the set mass fraction to total 100 g, the precisely weighed powders are put into a ball milling pot and 500 g of stainless steel grinding balls are added. The bowl was then sealed and the vacuum in the bowl was reduced to 10 using a vacuum pump 4 Pa, dry ball milling is carried out for 1 hour at a rotating speed of 300rpm, and then sieving is carried out, so that M2 high-speed steel-titanium carbide composite powder with mass fractions of 0wt%, 10wt%, 20wt%, 30wt%, 40wt%, 50wt%, 60wt% and 70wt% of titanium carbide hard phase is obtained. Then, a dense insulating alumina tube with an inner diameter of 11.4mm, an outer diameter of 16.4mm and a height of 20mm is sleeved in a metal mold with an inner diameter of 16.4mm, an outer diameter of 40mm and a height of 20mm, and a high-purity tungsten block with a diameter of 11.4mm and a height of 10mm is sleeved in the alumina tube to be used as a lower pressure head electrode. Then 6 g of composite powder with different hard phases of titanium carbide are filled into an alumina tube, and a high-purity tungsten block with the diameter of 11.4mm and the height of 20mm is filled above the powder to be used as an upper pressure head electrode, so as to form a sintering assembly. The sintering assembly is installed in a hydraulic system and connected with a pulse power supply, and the hydraulic system is insulated from the pulse power supply and respectively applies 500MPa pressure and 4.8X10 to the powder blank through an upper pressure head electrode and a lower pressure head electrode 6 A/m 2 Pulsed current of current density and electric field of 1000V/m. And after the pulse current flash sintering is carried out for 30 seconds, the pulse power supply is turned off, the sintering assembly is taken down, and the sintering assembly is disassembled to obtain the M2 high-speed steel-titanium carbide hard alloy block materials with different fully compact titanium carbide hard paper phase mass fractions. The surface of the block material is polished to 100 mu m by 600-1500-mesh sand paper, and the thickness of the block material is polished to about 50 by 2000-mesh sand paperμm followed by polishing with a 3 μm diamond polishing solution. The vickers hardness was measured with a load of 50N in a vickers hardness tester for 10 seconds, and the measured results are shown in fig. 1, which shows that as the mass fraction of the titanium carbide hard phase in the M2 high-speed steel matrix increases, the hardness of the M2 high-speed steel-titanium carbide cemented carbide obtained by sintering also gradually increases.
Example 2
In this example, 80wt% of a micro-scale near-spherical M2 high-speed steel powder and 20wt% of titanium carbide powder were used as raw material powders. The two powders are weighed according to the set mass fraction to total 100 g, the precisely weighed powders are put into a ball milling pot and 500 g of stainless steel grinding balls are added. The bowl was then sealed and the vacuum in the bowl was reduced to 10 using a vacuum pump 4 Pa, dry ball milling was carried out at 300rpm for 1 hour, followed by sieving to obtain a composite powder. The compact insulating alumina tube with the inner diameter of 11.4mm, the outer diameter of 16.4mm and the height of 20mm is sleeved in a metal mould with the inner diameter of 16.4mm, the outer diameter of 40mm and the height of 20mm, and a high-purity tungsten block with the diameter of 11.4mm and the height of 10mm is arranged in the alumina tube to be used as a lower pressure head electrode. Then 6 g of the composite powder was charged into an alumina tube, and a high purity tungsten block having a diameter of 11.4mm and a height of 20mm was charged over the powder as an upper indenter electrode to constitute a sintered assembly. The sintering assembly was installed in a hydraulic system and connected to a pulsed power supply, which was insulated from the pulsed power supply but which applied a pressure of 500MPa and 4.6x10 to the powder compact via the ram electrodes, respectively 6 A/m 2 Pulsed current of current density and electric field of 1000V/m. And after the pulse current flash sintering is carried out for 30 seconds, the pulse power supply is turned off, the sintering assembly is taken down, and the sintering assembly is disassembled to obtain the fully compact 80wt% M2 high-speed steel-20 wt% titanium carbide steel bonded hard alloy block material. The resulting block was polished to a surface of 100 μm with 600, 1500 mesh sandpaper, and then polished to a thickness of about 50 μm with 2000 mesh sandpaper, followed by polishing with a diamond polishing liquid of 3 μm. The microstructure is observed through a field emission scanning electron microscope, and the result is shown as figure 2, which shows that the M2 high-speed steel-titanium carbide steel bonded hard alloy prepared by the method is completely compact, and the M2 high-speed steel matrix and the titanium carbide hard material are prepared by the methodThe combination is tight.
Example 3
In this example, 60wt% of the micro-scale near-spherical M2 high-speed steel powder and 40wt% of the titanium carbide powder were used as raw material powders. The two powders are weighed according to the set mass fraction to total 100 g, the precisely weighed powders are put into a ball milling pot and 500 g of stainless steel grinding balls are added. The bowl was then sealed and the vacuum in the bowl was reduced to 10 using a vacuum pump 4 Pa, dry ball milling was carried out at 300rpm for 1 hour, followed by sieving to obtain a composite powder. The compact insulating alumina tube with the inner diameter of 11.4mm, the outer diameter of 16.4mm and the height of 20mm is sleeved in a metal mould with the inner diameter of 16.4mm, the outer diameter of 40mm and the height of 20mm, and a high-purity tungsten block with the diameter of 11.4mm and the height of 10mm is arranged in the alumina tube to be used as a lower pressure head electrode. Then 6 g of the composite powder was charged into an alumina tube, and a high purity tungsten block having a diameter of 11.4mm and a height of 20mm was charged over the powder as an upper indenter electrode to constitute a sintered assembly. The sintering assembly was installed in a hydraulic system and connected to a pulsed power supply, which was insulated from the pulsed power supply but which applied a pressure of 500MPa and a pressure of 4.7x10 to the powder compact via the ram electrodes, respectively 6 A/m 2 Pulse current with current density and an electric field of 1000V/M are respectively subjected to pulse current flash sintering for 10 seconds, 15 seconds, 20 seconds, 25 seconds, 30 seconds, 35 seconds, 40 seconds, 45 seconds and 50 seconds, a pulse power supply is turned off, a sintering assembly is taken down, the sintering assembly is disassembled to obtain 60wt% M2 high-speed steel-40 wt% titanium carbide steel bonded hard alloy block materials with different densities, the densities of the steel bonded hard alloy blocks with different sintering times are measured by using an Archimedes drainage method, and the result is shown in figure 3, wherein the M2 high-speed steel-titanium carbide steel bonded hard alloy achieves densification of approximately 98% in the first 10 seconds of flash sintering, and the density of the M2 high-speed steel-titanium carbide steel bonded hard alloy gradually rises to almost complete densification along with the time as the sintering time increases to 30 seconds. Further lengthening the sintering time to 45 seconds, the densification degree of the M2 high-speed steel-titanium carbide steel bonded hard alloy block approaching full densification within 30 seconds to 45 seconds is almost unchanged, because the fine pores between the matrix and the hard phase in the block are gradually closed, while the overall density of the block is ensuredAnd the stability is maintained. The sintering time is prolonged continuously, and the high-density M2 high-speed steel liquid phase in the M2 high-speed steel-titanium carbide steel bonded hard alloy is lost from the system due to high pressure, so that the overall density of the system is reduced.
Example 4
In this example, 40wt% of a micro-scale near-spherical M2 high-speed steel powder and 60wt% of titanium carbide powder were used as raw material powders. The two powders are weighed according to the set mass fraction to total 100 g, the precisely weighed powders are put into a ball milling pot and 500 g of stainless steel grinding balls are added. The bowl was then sealed and the vacuum in the bowl was reduced to 10 using a vacuum pump 4 Pa, dry ball milling was carried out at 300rpm for 1 hour, followed by sieving to obtain a composite powder. The compact insulating alumina tube with the inner diameter of 11.4mm, the outer diameter of 16.4mm and the height of 20mm is sleeved in a metal mould with the inner diameter of 16.4mm, the outer diameter of 40mm and the height of 20mm, and a high-purity tungsten block with the diameter of 11.4mm and the height of 10mm is arranged in the alumina tube to be used as a lower pressure head electrode. Then 6 g of the composite powder was charged into an alumina tube, and a high purity tungsten block having a diameter of 11.4mm and a height of 20mm was charged over the powder as an upper indenter electrode to constitute a sintered assembly. The sintering assembly was installed in a hydraulic system and connected to a pulsed power supply, which was insulated from the pulsed power supply but which applied a pressure of 500MPa and a pressure of 4.8x10 to the powder compact via the ram electrodes, respectively 6 A/m 2 The temperature of the green powder body was measured by an S-type thermocouple during sintering with a pulse current of current density and an electric field of 1000V/m, and the temperature change curve is shown in FIG. 4, which shows that the initial 5 second temperature rise rate during sintering can reach about 500 ℃/S, the temperature reaches a peak value of about 1300 ℃ at about 10 seconds, and then the temperature is slightly reduced to about 1200 ℃ and remains stable until the pulse power supply is turned off and the temperature is rapidly reduced. The temperature rising rate of the sintering process of the powder green compact can form a liquid phase under the condition of being lower than the melting point (about 1500 ℃) of steel-based powder and form strong interface combination with titanium carbide hard phase in extremely short time. The pulse power supply is turned off after the pulse current flash sintering is carried out for 50 seconds, the sintering assembly is taken down after the temperature of the sintering assembly is further waited to be reduced, and the sintering assembly is disassembled to obtain the fully compact 40wt percent M2 high-speed steel-60 wt percent titanium carbide steel-bonded hardAlloy block materials.
Example 5
In this example, 10wt% of a micro-scale near-spherical M2 high-speed steel powder and 90wt% of titanium carbide powder were used as raw material powders. The two powders are weighed according to the set mass fraction to total 100 g, the precisely weighed powders are put into a ball milling pot and 500 g of stainless steel grinding balls are added. The bowl was then sealed and the vacuum in the bowl was reduced to 10 using a vacuum pump 4 Pa, dry ball milling was carried out at 300rpm for 1 hour, followed by sieving to obtain a composite powder. The compact insulating alumina tube with the inner diameter of 11.4mm, the outer diameter of 16.4mm and the height of 20mm is sleeved in a metal mould with the inner diameter of 16.4mm, the outer diameter of 40mm and the height of 20mm, and a high-purity tungsten block with the diameter of 11.4mm and the height of 10mm is arranged in the alumina tube to be used as a lower pressure head electrode. Then 6 g of the composite powder was charged into an alumina tube, and a high purity tungsten block having a diameter of 11.4mm and a height of 20mm was charged over the powder as an upper indenter electrode to constitute a sintered assembly. The sintering assembly was installed in a hydraulic system and connected to a pulsed power supply, which was insulated from the pulsed power supply but which applied a pressure of 500MPa and 5.2x10 to the powder compact via the ram electrodes, respectively 6 A/m 2 Pulsed current of current density and an electric field of 1000V/m. And after the pulse current flash sintering is carried out for 30 seconds, the pulse power supply is turned off, the sintering assembly is taken down, and the sintering assembly is disassembled to obtain the fully compact 10wt% M2 high-speed steel-90 wt% titanium carbide steel bonded hard alloy block material. The compressive stress strain curve obtained by cutting the block material into cylinders with the diameter of 3mm and the height of 5mm is shown in figure 5, wherein the compressive strength of 10wt% of M2 high-speed steel-90 wt% of titanium carbide steel bonded hard alloy block material can reach 4300MPa, which is far higher than the compressive strength of 3250MPa of M2 high-speed steel, which means that the interface combination of the matrix and the hard phase of 90wt% of M2 high-speed steel-10 wt% of titanium carbide steel bonded hard alloy block material is good, and the compressive property is superior to that of M2 high-speed steel block.
Example 6
In this example, 5wt% of a micro-scale near-spherical M2 high-speed steel powder and 95wt% of titanium carbide powder were used as raw material powders. Weighing the two powders according to a set mass fraction100 grams of the precisely weighed powder was charged into a ball milling jar and 500 grams of stainless steel milling balls were added. The bowl was then sealed and the vacuum in the bowl was reduced to 10 using a vacuum pump 4 Pa, dry ball milling was carried out at 300rpm for 1 hour, followed by sieving to obtain a composite powder. The compact insulating alumina tube with the inner diameter of 11.4mm, the outer diameter of 16.4mm and the height of 20mm is sleeved in a metal mould with the inner diameter of 16.4mm, the outer diameter of 40mm and the height of 20mm, and a high-purity tungsten block with the diameter of 11.4mm and the height of 10mm is arranged in the alumina tube to be used as a lower pressure head electrode. Then 6 g of the composite powder was charged into an alumina tube, and a high purity tungsten block having a diameter of 11.4mm and a height of 20mm was charged over the powder as an upper indenter electrode to constitute a sintered assembly. The sintering assembly was installed in a hydraulic system and connected to a pulsed power supply, which was insulated from the pulsed power supply but which applied a pressure of 500MPa and 1.2x10 to the powder compact via the ram electrodes, respectively 6 A/m 2 、2.2×10 6 A/m 2 、3.2×10 6 A/m 2 、4.2×10 6 A/m 2 、5.2×10 6 A/m 2 Pulsed current of current density and an electric field of 1000V/m. And after the pulse current flash sintering is carried out for 30 seconds, the pulse power supply is turned off, the sintering assembly is taken down, and the sintering assembly is disassembled to obtain the 5wt% of the M2 high-speed steel-95 wt% of the titanium carbide steel bonded hard alloy block material. The relative densities of the block materials obtained by measuring different current densities through the Archimedes drainage method are respectively as follows: 70.51%, 83.23%, 90.75%, 99.78% and 94.83%. Example 6 demonstrates that pulse currents of higher current densities within a range can achieve higher densification of a cemented carbide powder green compact, but when the current densities are too high, the low melting point, high density steel matrix in the cemented carbide system will be "lost" from the system, resulting in a reduced density of the cemented carbide block being produced, but the bond between the M2 steel matrix and the titanium carbide hard phase remains tight.
Example 7
In this example, 30wt% of a micro-scale near-spherical M2 high-speed steel powder and 75wt% of titanium carbide powder were used as raw material powders. Weighing the two powders according to a set mass fraction to obtain 100 g, loading the precisely weighed powders into a ball milling pot, and adding 500 gStainless steel grinding ball. The bowl was then sealed and the vacuum in the bowl was reduced to 10 using a vacuum pump 4 Pa, dry ball milling was carried out at 300rpm for 1 hour, followed by sieving to obtain a composite powder. The compact insulating alumina tube with the inner diameter of 11.4mm, the outer diameter of 16.4mm and the height of 20mm is sleeved in a metal mould with the inner diameter of 16.4mm, the outer diameter of 40mm and the height of 20mm, and a high-purity tungsten block with the diameter of 11.4mm and the height of 10mm is arranged in the alumina tube to be used as a lower pressure head electrode. Then 6 g of the composite powder was charged into an alumina tube, and a high purity tungsten block having a diameter of 11.4mm and a height of 20mm was charged over the powder as an upper indenter electrode to constitute a sintered assembly. The sintering assembly is installed in a hydraulic system and connected with a pulse power supply, and the hydraulic device is insulated from the pulse power supply and respectively applies pressures of 50MPa, 150MPa, 250MPa, 350MPa, 450MPa and 550MPa and 3.2X10 to the powder blank through a pressure head electrode 6 A/m 2 Pulsed current of current density and an electric field of 1000V/m. And after the pulse current flash sintering is carried out for 30 seconds, the pulse power supply is turned off, the sintering assembly is taken down, and the sintering assembly is disassembled to obtain 30wt% of M2 high-speed steel-75 wt% of titanium carbide steel bonded hard alloy block material. The relative densities of the block materials obtained by measuring different current densities through the Archimedes drainage method are respectively as follows: 95.21%, 94.63%, 93.52%, 96.22%, 99.95%, 99.91%. Example 7 demonstrates that under constant current density conditions, lower pressures result in greater contact resistance between powder particles and thus higher sintering temperatures, and the resulting bulk material has a relatively high density, but does not allow for complete densification of the cemented carbide block. The contact resistance between powders is reduced by increasing the pressure step by step, and the sintering temperature under the action of the pulse current with the same current density is relatively reduced, so that the density of the prepared block is relatively lower. The pressure is further increased, the liquid-phase steel base produced in the sintering process flows more fully under the action of high pressure and fills the gaps among the hard phase particles, and finally the nearly fully compact steel-bonded hard alloy block is obtained.
Example 8
In this example, 20wt% of micron-sized spherical 316L stainless steel powder and 80wt% of titanium carbide powder were used as raw material powders. Will beThe two powders are weighed according to the set mass fraction to total 100 g, the precisely weighed powders are put into a ball milling pot and 500 g of stainless steel grinding balls are added. The bowl was then sealed and the vacuum in the bowl was reduced to 10 using a vacuum pump 4 Pa, dry ball milling was carried out at 300rpm for 1 hour, followed by sieving to obtain a composite powder. The compact insulating alumina tube with the inner diameter of 11.4mm, the outer diameter of 16.4mm and the height of 20mm is sleeved in a metal mould with the inner diameter of 16.4mm, the outer diameter of 40mm and the height of 20mm, and a high-purity tungsten block with the diameter of 11.4mm and the height of 10mm is arranged in the alumina tube to be used as a lower pressure head electrode. Then 6 g of the composite powder was charged into an alumina tube, and a high purity tungsten block having a diameter of 11.4mm and a height of 20mm was charged over the powder as an upper indenter electrode to constitute a sintered assembly. The sintering assembly was installed in a hydraulic system and connected to a pulsed power supply, which was insulated from the pulsed power supply but which applied a pressure of 450MPa and a pressure of 3.2X10, respectively, to the powder compact via the ram electrodes 6 A/m 2 Pulsed current of current density and an electric field of 1000V/m. Pulse current flash sintering is carried out for 30 seconds, 60 seconds, 90 seconds and 120 seconds, then a pulse power supply is turned off, the sintering component is taken down, and 20wt%316L stainless steel-80 wt% titanium carbide steel bonded hard alloy block materials are obtained through disassembly of the sintering component. The relative densities of the block materials obtained by measuring different current densities through the Archimedes drainage method are respectively as follows: 99.13%, 98.62%, 96.47% and 92.35%. Example 8 illustrates that under the condition of constant pressure and pulse current density, the density of 361L stainless steel-titanium carbide steel bonded hard alloy block material is reduced by prolonging the sintering time, which is mainly caused by the long-time high-temperature and high-pressure condition, the liquid phase formed by melting the low-melting-point high-density 316L stainless steel in the system is lost from the system, the relative mass fraction of the high-melting-point low-density titanium carbide in the system is increased, and the overall density of the system is reduced, so that reasonable regulation and control of the sintering time is crucial for preparing the high-performance steel bonded hard alloy.
While the foregoing description illustrates and describes the preferred embodiments of the present invention, it is to be understood that the invention is not limited to the forms disclosed herein, but is not to be construed as limited to other embodiments, and is capable of numerous other combinations, modifications and environments and is capable of changes or modifications within the scope of the inventive concept as expressed herein, either as a result of the foregoing teachings or as a result of the knowledge or technology of the relevant art. And that modifications and variations which do not depart from the spirit and scope of the invention are intended to be within the scope of the appended claims.
Claims (10)
1. A method of making a steel-based-metal carbon/nitride steel cemented carbide, the method comprising the steps of:
s1, mixing and ball milling steel-based powder and metal carbo/nitride to obtain uniformly mixed composite powder;
s2, loading the uniformly mixed composite powder into an alumina tube, and applying pulse current with certain pressure and current density to the composite powder through an upper pressure head electrode and a lower pressure head electrode to finish the rapid densification and interface reaction process;
s3, after a set time, cutting off pulse current to enable the block obtained by sintering the composite powder to be cooled rapidly, and obtaining the steel base-metal carbon/nitride steel bonded hard alloy block.
2. The method of making a steel matrix-metal carbonitride steel cemented carbide according to claim 1, wherein the steel matrix is M2 high speed steel or other types of high speed steel, high manganese steel, stainless steel, heat resistant steel, tool steel or carbon steel powder.
3. The method of making a steel-based metal carbide/nitride steel bond cemented carbide according to claim 2, wherein the metal carbide/nitride is titanium carbide, titanium nitride, tungsten carbide, tantalum carbide or tantalum nitride powder.
4. A method of producing a steel-based metal carbo/nitride cemented carbide according to claim 3, wherein S1 comprises in particular: mixing steel-based powder with a certain mass and metal/nitride powder with a certain mass according to a certain mass ratio, and carrying out dry vacuum ball milling to obtain the composite powder, wherein the mass fraction of the steel-based powder in the composite powder is 5-95 wt%, and the mass fraction of the metal carbon/nitride powder is 5-95 wt%.
5. The method of making a steel-based metal carbide/nitride steel bond cemented carbide according to claim 4, wherein the ranges of pressure and current densities are respectively: pressure: 50-550 MPa, current density: 1.2 to 5.2X10 6 A/m 2 Electric field strength: 500-3500V/m.
6. The method of producing steel-based metal carbide/nitride steel cemented carbide according to claim 1, wherein the set time is 10-120 seconds.
7. The method for producing steel-based metal carbonitride steel-bonded cemented carbide according to claim 5, wherein the pressure is 500MPa and the current density of the pulse current is 4.8 x 10 6 A/m 2 The electric field strength was 1000V/m.
8. The method for producing a steel-based metal carbonitride steel-bonded cemented carbide according to claim 4, wherein when the metal carbonitride is titanium carbide, the mass fraction of the titanium carbide powder in the mixed powder is 10wt%, 20wt%, 30wt%, 40wt%, 50wt%, 60wt% or 70wt%.
9. Steel-based-metal carbon/nitride steel bonded cemented carbide, characterized in that the alloy is obtained by the method according to any one of claims 1-8.
10. The steel-bonded cemented carbide according to claim 9, wherein the relative density of the steel-bonded cemented carbide mass is not less than 99.5%, the vickers hardness is 200-2000 Hv, and the compressive strength is 400-4500 MPa.
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