CN106868372B - A kind of preparation method of MoFeB based metal ceramic coatings - Google Patents
A kind of preparation method of MoFeB based metal ceramic coatings Download PDFInfo
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- 239000002184 metal Substances 0.000 title claims abstract description 33
- 229910052751 metal Inorganic materials 0.000 title claims abstract description 33
- 238000005524 ceramic coating Methods 0.000 title claims abstract description 15
- 238000002360 preparation method Methods 0.000 title claims abstract description 11
- 239000000843 powder Substances 0.000 claims abstract description 123
- 238000005245 sintering Methods 0.000 claims abstract description 50
- 239000002994 raw material Substances 0.000 claims abstract description 21
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims abstract description 18
- 229910052786 argon Inorganic materials 0.000 claims abstract description 9
- 239000007789 gas Substances 0.000 claims abstract description 9
- 238000002156 mixing Methods 0.000 claims abstract description 3
- 238000000498 ball milling Methods 0.000 claims description 10
- 239000000463 material Substances 0.000 claims description 10
- 238000010438 heat treatment Methods 0.000 claims description 9
- 238000000034 method Methods 0.000 claims description 9
- 229910000831 Steel Inorganic materials 0.000 claims description 5
- 239000010959 steel Substances 0.000 claims description 5
- 239000011324 bead Substances 0.000 claims description 4
- 238000000227 grinding Methods 0.000 claims description 4
- 238000002791 soaking Methods 0.000 claims description 4
- 229910001220 stainless steel Inorganic materials 0.000 claims description 4
- 239000010935 stainless steel Substances 0.000 claims description 4
- 239000000919 ceramic Substances 0.000 abstract description 16
- 230000000694 effects Effects 0.000 abstract description 5
- 229910052761 rare earth metal Inorganic materials 0.000 abstract description 4
- 150000002910 rare earth metals Chemical class 0.000 abstract description 3
- 230000009286 beneficial effect Effects 0.000 abstract 1
- 238000009837 dry grinding Methods 0.000 abstract 1
- 238000001914 filtration Methods 0.000 abstract 1
- 238000007873 sieving Methods 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 11
- 230000000052 comparative effect Effects 0.000 description 7
- 238000007599 discharging Methods 0.000 description 5
- 230000008569 process Effects 0.000 description 5
- 238000005516 engineering process Methods 0.000 description 3
- HXQQNYSFSLBXQJ-UHFFFAOYSA-N COC1=C(NC(CO)C(O)=O)CC(O)(CO)CC1=NCC(O)=O Chemical compound COC1=C(NC(CO)C(O)=O)CC(O)(CO)CC1=NCC(O)=O HXQQNYSFSLBXQJ-UHFFFAOYSA-N 0.000 description 2
- 238000005299 abrasion Methods 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 239000011248 coating agent Substances 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 239000003963 antioxidant agent Substances 0.000 description 1
- 230000003078 antioxidant effect Effects 0.000 description 1
- 235000006708 antioxidants Nutrition 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 150000001639 boron compounds Chemical class 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000003153 chemical reaction reagent Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000001192 hot extrusion Methods 0.000 description 1
- 238000002347 injection Methods 0.000 description 1
- 239000007924 injection Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000011068 loading method Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000008092 positive effect Effects 0.000 description 1
- 239000004575 stone Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000003786 synthesis reaction 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
- C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
- C22C27/04—Alloys based on tungsten or molybdenum
-
- 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
- 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
- B22F3/12—Both compacting and sintering
- B22F3/16—Both compacting and sintering in successive or repeated steps
-
- 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
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- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
- C01B35/00—Boron; Compounds thereof
- C01B35/02—Boron; Borides
- C01B35/04—Metal borides
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0084—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ carbon or graphite as the main non-metallic constituent
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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
- 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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- 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
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
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Abstract
The present invention provides a kind of preparation method of MoFeB based metal ceramic coatings, includes the following steps：(1) dispensing is formed by following raw material：7.0 11.2 parts of Fe powder, 28.0 32.0 parts of FeB powder, 46.0 48.0 parts of Mo powder, 12 parts of Y powder, 23 parts of Cr powder, 24 parts of Ni powder, 24 parts of Mn powder, 12 parts of C powder；(2) raw material of step (1) is crushed with ball mill, mixing, argon gas atmosphere dry grinding, sieving filtering；(3) raw material powder prepared by step (2) is sintered in SPS sintering furnaces, sintering schedule：Powder is fitted into mold and is put into SPS sintering furnaces by room temperature, by discharge plasma sintering, is kept the temperature, is cooled to room temperature with the furnace；Vacuum is kept in furnace body.The beneficial effects of the invention are as follows " the rare earth effects " using Y, improve Mo on the whole2FeB2The hardness of based ceramic metal, toughness simultaneously improve its consistency and porosity.
Description
Technical field
The invention belongs to material chemistry technical field, more particularly, to a kind of preparation side of MoFeB based metal ceramic coatings
Method.
Background technology
Steel and iron industry is the basis of Chinese national economy, " foundation stone " of industrial development and mold is known as.With science
Technology high-speed develops and the deterioration of mold work environment, simple metal material cannot meet the requirement of die industry.Mould
The failure mode of tool is generally plastically deformed, abrasion, fracture or cracking, metal fatigue and corrosion etc..And it is mould wherein to wear
Has the principal mode of disabling damage.And consider that die surface is modified and surface is strong from economic benefit and energy resources utilization rate
Change is the only selection for improving mold performance and extending die life.
Ternary Boride Base Cermets are a kind of new materials of function admirable, there is very big development potentiality.Ternary boron
Compound based ceramic metal has high intensity, hardness, fracture strength and excellent heat resistance and corrosion resistance, therefore
Be usually applied to injection machine part, copper the contour abrasion of hot-extrusion mold environment in.Wherein Mo2FeB2Based ceramic metal was both
The characteristics such as high intensity, high rigidity, wear-resistant, high temperature resistant, the anti-oxidant and chemical stability of ceramics are maintained, and with preferable
Metal toughness and plasticity, but also good metallurgical binding can be generated with steel matrix, therefore be that die surface is modified
Suitable material selection.
Invention content
The purpose of the present invention is to further improve Mo2FeB2The comprehensive performance of based ceramic metal improves its hardness simultaneously
And toughness, to provide better material selection for mold surface modification of steel.By adding appropriate simple substance Y powder in the feed, Y's
" rare earth effect " can effectively reduce Mo2FeB2The grain size of based ceramic metal, while rare earth element activity is big easily and impurity
Element combines and discharges the presence to reduce impurity content and defect, so as to improve Mo on the whole2FeB2Based ceramic metal
Hardness, toughness simultaneously improve its consistency and porosity.
The technical scheme is that：A kind of Mo2FeB2The preparation method of based metal ceramic coating, includes the following steps：
(1) dispensing is formed by following raw material：7.0-11.2 parts of Fe powder, 28.0-32.0 parts of FeB powder, Mo powder 46.0-48.0
Part, 1.0-2.0 parts of Y powder, 2.0-3.0 parts of Cr powder, 2.0-4.0 parts of Ni powder, 2.0-4.0 parts of Mn powder, 1.0-2.0 parts of C powder；
(2) the bulky grain raw material of step (1) is crushed with mixing using ball mill, is done under argon gas atmosphere protection
Mill, then filters out bulky grain powder, wherein：The ball mill is ground using the stainless steel of a diameter of Ф 5mm and Ф 10mm
The mass ratio of ball, big ball and bead is 20-25:1, ratio of grinding media to material is 3-8:1, rotational speed of ball-mill 200-300r/min, Ball-milling Time
For 18-22h；
(3) the mixed raw material powder prepared by step (2) is sintered in discharge plasma sintering stove, sintering schedule is：
During room temperature, powder is fitted into mold and is put into SPS sintering furnaces, by discharge plasma sintering, and keeps the temperature, then cools to the furnace
Room temperature；Vacuum is kept in furnace body, wherein：Being sintered heating rate is：90-110 DEG C/min, sintering temperature is 900-1100 DEG C, is burnt
Knot pressure power is 25-35MPa, soaking time 5-15min；Vacuum degree control≤8Pa.
Preferably, the step (1) material purity >=99.00%；
Preferably, the step (2) is filtered using 160 mesh sieve；
Preferably, the planetary ball mill of the step (2) uses the stainless steel abrading-ball of a diameter of Ф 5mm or Ф 10mm,
The mass ratio of big ball and bead is 24:1, ratio of grinding media to material is 5:1, rotational speed of ball-mill 250r/min, Ball-milling Time 20h；
Preferably, the sintering schedule of the step (3)：Heating rate is 100 DEG C/min；Sintering temperature is 1050 DEG C；It burns
Knot pressure power is 30MPa；Soaking time is 10min；Vacuum degree control≤6Pa.
Preferably, the charge ratio of the step (1) is：10.1-11.1 parts of Fe powder, 28.0 parts of FeB powder, Mo powder 46.0-
47.0 parts, 1.0-1.5 parts of Y powder, 2-2.5 parts of Cr powder, 2.0-2.9 parts of Ni powder, 2.0-2.5 parts of Mn powder, 1.0-1.5 parts of C powder
Another aspect of the present invention further includes one kind Mo as made from the above method2FeB2Based metal ceramic coating.
Another aspect of the present invention further includes above-mentioned Mo2FeB2Based metal ceramic coating is in the application of mold steel surface.
The invention has the advantages and positive effects that：
(1) raw materials such as FeB powder, Fe powder, Mo powder, which all compare, used in is easy to get, and can effectively reduce production cost.
(2) by effectively adding simple substance Y powder, Y element can be with crystal grain thinning；Form intermetallic compound；Form oxide
The effects that, these improve the compactness and uniformity of metal-cermic coating, and significantly improve metal-cermic coating hardness,
The comprehensive performances such as consistency and toughness.
Specific embodiment
Pure Fe powder, FeB powder, Mo powder, Y powder and Cr powder, Ni powder, Mn powder and the C powder that the present invention uses are commercially availableization
It learns pure powder reagent, prior to ball milling 20h in QM-3SP4 type planetary ball mills after dispensing, dry grinds under argon gas atmosphere protection, mistake
Sieve；Then powder is fitted into mold to be put into SPS sintering furnaces, by discharge plasma sintering, and keeps the temperature, then cool to the furnace
Room temperature；Vacuum is kept in furnace body.
The principle of the present invention is by adding appropriate Y powder, with crystal grain thinning and can be improved using " the rare earth effect " of Y element
Consistency and knot porosity.By adding Y powder, Mo2FeB2Tensile strength, hardness and the consistency of based ceramic metal have aobvious
The raising or improvement of work.The present invention is in order to make Mo2FeB2There is best comprehensive performance in based ceramic metal, so addition is appropriate
Cr powder, Ni powder, Mn powder, while in order to reduce oxidation of raw material etc., add a small amount of C powder.
Comparative example
With 12.1 parts of Fe powder, 30.9 parts of FeB powder, 48.0 parts of Mo powder, 2.5 parts of Cr powder, 2.9 parts of Ni powder, 2.5 parts of Mn powder, C powder
1.0 parts of progress dispensings, but Y powder is not added.By above-mentioned raw materials prior to 250r/min ball millings in QM-3SP4 type planetary ball mills
20h dry grinds under argon gas atmosphere protection, is sieved；Prepared mixed raw material powder is burnt in plasma discharging (SPS) sintering furnace
Knot.During room temperature, powder is fitted into mold and is put into SPS sintering furnaces, by discharge plasma sintering, and is kept the temperature, then with furnace cooling
But to room temperature；Vacuum is kept in furnace body in the process.Sintering schedule is：Heating rate is 100 DEG C/min；Sintering temperature is 1050
℃；Sintering pressure is 30Mpa；Keep the temperature 10min；Vacuum degree control≤6pa.
Embodiment 1
With 11.1 parts of Fe powder, 30.9 parts of FeB powder, 48.0 parts of Mo powder, 1.0 parts of Y powder, 2.5 parts of Cr powder, 2.9 parts of Ni powder, Mn powder
2.5 parts, 1.0 parts of progress dispensings of C powder.By above-mentioned raw materials prior to 250r/min ball milling 20h in QM-3SP4 type planetary ball mills,
It dry grinds, is sieved under argon gas atmosphere protection；Prepared mixed raw material powder is sintered in plasma discharging (SPS) sintering furnace.
During room temperature, powder is fitted into mold and is put into SPS sintering furnaces, by discharge plasma sintering, and keeps the temperature, then cools to the furnace
Room temperature；Vacuum is kept in furnace body in the process.Sintering schedule is：Heating rate is 100 DEG C/min；Sintering temperature is 1050 DEG C；It burns
Knot pressure power is 30Mpa；Keep the temperature 10min；Vacuum degree control≤6pa.
Embodiment 2
With 10.1 parts of Fe powder, 30.9 parts of FeB powder, 48.0 parts of Mo powder, 2.0 parts of Y powder, 2.5 parts of Cr powder, 2.9 parts of Ni powder, Mn powder
2.5 parts, 1.0 parts of progress dispensings of C powder.By above-mentioned raw materials prior to 250r/min ball milling 20h in QM-3SP4 type planetary ball mills,
It dry grinds, is sieved under argon gas atmosphere protection；Prepared mixed raw material powder is sintered in plasma discharging (SPS) sintering furnace.
During room temperature, powder is fitted into mold and is put into SPS sintering furnaces, by discharge plasma sintering, and keeps the temperature, then cools to the furnace
Room temperature；Vacuum is kept in furnace body in the process.Sintering schedule is：Heating rate is 90 DEG C/min；Sintering temperature is 900 DEG C；Sintering
Pressure is 30Mpa；Keep the temperature 10min；Vacuum degree control≤6pa.
Embodiment 3
With 7.0 parts of Fe powder, 32.0 parts of FeB powder, 46.0 parts of Mo powder, 2.0 parts of Y powder, 3.0 parts of Cr powder, 4.0 parts of Ni powder, Mn powder
4.0 parts, 2.0 parts of progress dispensings of C powder.By above-mentioned raw materials prior to 250r/min ball milling 20h in QM-3SP4 type planetary ball mills,
It dry grinds, is sieved under argon gas atmosphere protection；Prepared mixed raw material powder is sintered in plasma discharging (SPS) sintering furnace.
During room temperature, powder is fitted into mold and is put into SPS sintering furnaces, by discharge plasma sintering, and keeps the temperature, then cools to the furnace
Room temperature；Vacuum is kept in furnace body in the process.Sintering schedule is：Heating rate is 110 DEG C/min；Sintering temperature is 1100 DEG C；It burns
Knot pressure power is 25Mpa；Keep the temperature 5min；Vacuum degree control≤8pa.
Embodiment 4
With 11.2 parts of Fe powder, 28.0 parts of FeB powder, 47.0 parts of Mo powder, 1.5 parts of Y powder, 2.0 parts of Cr powder .02 parts of Ni powder, Mn powder
2.0 parts, 1.5 parts of progress dispensings of C powder.By above-mentioned raw materials prior to 250r/min ball milling 20h in QM-3SP4 type planetary ball mills,
It dry grinds, is sieved under argon gas atmosphere protection；Prepared mixed raw material powder is sintered in plasma discharging (SPS) sintering furnace.
During room temperature, powder is fitted into mold and is put into SPS sintering furnaces, by discharge plasma sintering, and keeps the temperature, then cools to the furnace
Room temperature；Vacuum is kept in furnace body in the process.Sintering schedule is：Heating rate is 100 DEG C/min；Sintering temperature is 1050 DEG C；It burns
Knot pressure power is 35Mpa；Keep the temperature 15min；Vacuum degree control≤6pa.
Above example is sufficiently mixed metal powder using mechanical ball mill mode, then carries out discharge plasma sintering
(SPS) a series of technology paths.
The present invention measures microhardness, loaded load 100gf, when loading stops using the types of MH -6 microhardness testers
Between be 10s；Using the special balance of SHIMADZUAUY120 types, the consistency of sample is measured according to Archimedes's drainage；It adopts
The porosity of sample is determined with model OLYMPUSGX51 types metallographic microscope according to ISO4505 standards；Using model WDW-
20 micro-control electronic universal testers carry out extension test, determine the yield strength and tensile strength of sample.
Measure comparative example and the Mo of embodiment 1-42FeB2The surface Vickers hardness of based ceramic metal, obtains following number
According to：In the feed without the Mo of addition Y powder2FeB2The comparative example surface Vickers hardness of based ceramic metal is 1167HV, is added
The Mo of Y powder2FeB2The average value of the embodiment 1-4 surfaces Vickers hardness of based ceramic metal has reached 1726-1889HV.
Measure comparative example and the Mo of embodiment 1-42FeB2The consistency of based ceramic metal, obtains data below：Comparison
The consistency of embodiment is 7.49g/cm3；The consistency mean value of embodiment 1-4 has reached 7.90-8.23g/cm3。
Measure comparative example and the Mo of embodiment 1-42FeB2The porosity of based ceramic metal, obtains data below：Comparison
The porosity of embodiment has 5.45%, and the porosity mean value of embodiment 1-4 is reduced to 2.90%-3.11%.
Measure comparative example and the Mo of embodiment 1-42FeB2The yield strength and tensile strength of based ceramic metal, obtain
Data below：The yield strength and tensile strength of comparative example are respectively 13.51 and 58.11Mpa, the surrender of embodiment 1-4
Intensity and tensile strength mean value difference 22.15Mpa-23.75Mpa and 114.86-116.32Mpa.
By above-mentioned comparison, the Mo after present invention addition Y powder is fully demonstrated2FeB2The mechanics synthesis of based ceramic metal
Performance has obtained large increase, and performance is more excellent.
One embodiment of the present of invention is described in detail above, but the content is only the preferable implementation of the present invention
Example, it is impossible to be construed as limiting the practical range of the present invention.All all the changes and improvements made according to the present patent application range
Deng, should all still belong to the present invention patent covering scope within.
Claims (8)
1. a kind of preparation method of MoFeB based metal ceramic coatings, it is characterised in that：Include the following steps：
(1) dispensing is formed by following raw material：7.0-11.2 parts of Fe powder, 28.0-32.0 parts of FeB powder, 46.0-48.0 parts of Mo powder, Y powder
1.0-2.0 parts, 2.0-3.0 parts of Cr powder, 2.0-4.0 parts of Ni powder, 2.0-4.0 parts of Mn powder, 1.0-2.0 parts of C powder；
(2) the bulky grain raw material of step (1) is crushed with mixing using ball mill, dry grinded under argon gas atmosphere protection, with
Bulky grain powder is filtered out afterwards, wherein：The ball mill uses the stainless steel abrading-ball of a diameter of Ф 5mm and Ф 10mm, greatly
The mass ratio of ball and bead is 20-25:1, ratio of grinding media to material is 3-8:1, rotational speed of ball-mill 200-300r/min, Ball-milling Time 18-
22h；
(3) the mixed raw material powder prepared by step (2) is sintered in discharge plasma sintering stove, sintering schedule is：Room temperature
When, powder is fitted into mold and is put into SPS sintering furnaces, by discharge plasma sintering, and keeps the temperature, then cools to room with the furnace
Temperature；Vacuum is kept in furnace body, wherein：Being sintered heating rate is：90-110 DEG C/min, sintering temperature is 900-1100 DEG C, sintering
Pressure is 25-35MPa, soaking time 5-15min；Vacuum degree control≤8Pa.
2. a kind of preparation method of MoFeB based metal ceramic coatings according to claim 1, it is characterised in that：The step
Suddenly (1) material purity >=99.00%.
3. a kind of preparation method of MoFeB based metal ceramic coatings according to claim 1, it is characterised in that：The step
Suddenly (2) are filtered using 160 mesh sieve.
4. a kind of preparation method of MoFeB based metal ceramic coatings according to claim 1, it is characterised in that：The step
Suddenly the planetary ball mill of (2) uses the stainless steel abrading-ball of a diameter of Ф 5mm or Ф 10mm, and the mass ratio of big ball and bead is
24:1, ratio of grinding media to material is 5:1, rotational speed of ball-mill 250r/min, Ball-milling Time 20h.
5. a kind of preparation method of MoFeB based metal ceramic coatings according to claim 1, it is characterised in that：The step
Suddenly the sintering schedule of (3)：Heating rate is 100 DEG C/min；Sintering temperature is 1050 DEG C；Sintering pressure is 30MPa；Soaking time
For 10min；Vacuum degree control≤6Pa.
6. a kind of preparation method of MoFeB based metal ceramic coatings according to claim 1, it is characterised in that：The step
Suddenly the charge ratio in (1) is：10.1-11.1 parts of Fe powder, 28.0 parts of FeB powder, 46.0-47.0 parts of Mo powder, 1.0-1.5 parts of Y powder, Cr
2-2.5 parts of powder, 2.0-2.9 parts of Ni powder, 2.0-2.5 parts of Mn powder, 1.0-1.5 parts of C powder.
7. a kind of MoFeB based metal ceramic coatings as made from any one of claim 1-5 methods.
8. a kind of MoFeB based metal ceramic coatings as made from any one of claim 1-5 methods are in the application of mold steel surface.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710134416.6A CN106868372B (en) | 2017-03-08 | 2017-03-08 | A kind of preparation method of MoFeB based metal ceramic coatings |
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| CN109868382B (en) * | 2019-02-11 | 2020-08-18 | 西安交通大学 | Rare earth element modified Mo2FeB2Base cermet and method for preparing same |
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