CN110218928A - A kind of high-strength tenacity Mo2FeB2Based ceramic metal and preparation method thereof - Google Patents
A kind of high-strength tenacity Mo2FeB2Based ceramic metal and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a kind of high-strength tenacity Mo2FeB2Based ceramic metal and preparation method thereof, comprising the following steps: prepare mixed powder using Mo powder, FeB powder, Fe powder as raw material first, be placed in vacuum drying oven be pre-sintered after ball milling and drying, obtain with Mo2FeB2Intermediate reaction product based on hard phase；Then gained intermediate reaction product is crushed, obtains intermediate reaction product powder；It is configured to cermet mixed powder using gained intermediate reaction product powder, Fe powder, Cr powder, Ni powder and graphite powder as raw material again, through processes such as ball mill mixing, compression mouldings, final sintering is finally completed in a vacuum furnace, obtains the Mo with high-strength tenacity2FeB2Based ceramic metal；The cermet of this method preparation, bending strength and fracture toughness with higher, comprehensive mechanical property is preferable, and preparation method provided by the invention is easy to operate, has broad application prospects.
Description
Technical field
The present invention relates to a kind of high-strength tenacity Mo2FeB2Based ceramic metal and preparation method thereof belongs to PM technique neck
Domain.
Background technique
Mo2FeB2Based ceramic metal has the excellent wearability of magnesium-yttrium-transition metal boride, heat-resisting quantity and corrosion-resistant
Property, while there is similar thermal expansion coefficient with steel, with Mo2NiB2And WCoB based ceramic metal is low compared to not only preparation cost,
And there is relatively good comprehensive mechanical property.Therefore, application, such as injection molding machine are had begun in some wear-resisting, anti-corrosion occasions
Part, tank tool and copper extrusion die processed etc. are a kind of hard materials of great development prospect.However, hard phase crystal grain passes through
Anisotropic growth boride reticular structure easy to form, and this structure can hinder the filling of eutectic liquid relative porosity factor, hard
More hole is generated at the interface cohesion of matter phase and bonding phase, interface bond strength decline leads to the synthesis mechanical property of material
Can not be high, it is restricted its application range.
In order to solve above-mentioned deficiency, the preferable Mo of comprehensive mechanical property is prepared2FeB2Based ceramic metal has some grind
Study carefully personnel to be studied after accordingly.Mainly promote the consistency of material by following two approach at present: one is adjustment
Composition And Process parameter such as property of raw material, ball milling condition, heating rate etc..Such as the Chinese patent " one of Publication No. 2104451325A
Kind Mo2FeB2The preparation process of based ceramic metal ", this method is with high-purity Fe2B powder and Mo powder are raw material through vacuum ball mill mixing, mould
Molded, vacuum-sintering and etc., the hard phase crystal grain anisotropic growth for the cermet prepared is obvious, the synthesis of material
Mechanical property promotion is limited, and preparation cost substantial increase, is not suitable for industrial production.Another kind is by addition alloy member
Element such as Mn, Cr, Ni improves the wetability of system.Such as a kind of Chinese patent " low cost of Publication No. 106916986A
Mo2FeB2The preparation method of based ceramic metal ", this method are original with molybdenum-iron powder, ferro-boron powder, vanadium iron powder, carbonyl iron, Cr, Ni, C
Material, the Mo prepared using the method that reaction in-situ is sintered2FeB2Cermet is bonded in phase in Fe base by Cr, Ni, C and is occurred
Solid solution is to improve interface cohesion, to improve the wetability between two-phase.However, Mo2FeB2The microscopic structure shape of based ceramic metal
Looks are very sensitive to the type and content of addition alloying element, and such method is easy to produce brittle third phase, influences material
Structure and performance, and production process is not easy to control.
In view of the foregoing, in order to make Mo2FeB2Based ceramic metal can preferably be applied in more areas, it is necessary to
The further research of technology of preparing expansion to such material, develops a kind of high-strength tenacity Mo2FeB2The preparation of based ceramic metal
New method makes its not only consistency with higher, while comprehensive mechanical property with higher, and is suitable for industrial metaplasia
It produces.
Summary of the invention
Goal of the invention: it is an object of the present invention to provide a kind of high-strength tenacity Mo2FeB2Based ceramic metal and preparation method thereof, solution
Determined existing Mo2FeB2The problem that based ceramic metal consistency is relatively low, comprehensive mechanical property is not high.
The present invention is achieved through the following technical solutions: a kind of high-strength tenacity Mo of the present invention2FeB2Based ceramic metal, tool
There are shaft-like hard-phase particles and the Fe base bonding phases such as core-ring structure is close；The core of the hard-phase particles is Mo2FeB2Particle,
The circular phase of the hard-phase particles core periphery is Mo2(Fe,Cr)B2Complicated solid solution.
The Mo2FeB2The component of the mass fraction of base metal-ceramic material are as follows: Mo:44.4~48.0 part, B:4.9~5.3
Part, Fe:41.2~44.9 part, Cr:2.2~2.8 part, Ni:2.6~3.2 part, C:0.1~0.4 part.
The high-strength tenacity Mo2FeB2Based ceramic metal is prepared via a method which:
(A) using Mo powder, FeB powder, Fe powder as raw material preparation mixed powder, in the mixed powder, in terms of mass parts, Mo:
48.0~51.9, Fe:42.4~46.7, B:5.3~5.7；Wherein, the granularity of Mo powder is 3.5~4.0 μm, and the granularity of FeB powder is
45.0~50.0 μm, the granularity of Fe powder is 3.0~3.5 μm；
(B) above-mentioned mixed powder is higher than 1.0 × 10 in vacuum degree after ball mill mixing, drying sieving-1The vacuum of Pa is burnt
Vacuum pre-sintering is carried out in freezing of a furnace, sintering temperature is 1000 DEG C, and soaking time 1h obtains intermediate reaction product；
(C) intermediate reaction product is crushed and obtains intermediate reaction product powder；
(D) intermediate reaction product powder, Fe powder, Cr powder, Ni powder and graphite powder are mixed and obtains secondary mixed powder, it is described
In secondary mixed powder, in terms of mass parts, Mo:44.4~48.0, B:4.9~5.3, Fe:41.2~44.9, Cr:2.2~2.8,
Ni:2.6~3.2, C:0.1~0.4；Wherein, the granularity of intermediate reaction product powder is 1.0~5.0 μm, and the granularity of Fe powder is
3.0~3.5 μm, the granularity of Cr powder is 4.5~5.0 μm, and the granularity of Ni powder is 3.0~3.5 μm, the granularity of graphite powder is 3.0~
4.0μm；
(E) by secondary mixed powder through ball mill mixing, be pressed into green compact after vacuum-sintering is carried out in vacuum sintering furnace；Institute
State vacuum-sintering process are as follows: green compact is warming up to 1200~1240 DEG C with the heating rate of 10 DEG C/min first, is not kept the temperature；Then
1140~1160 DEG C are cooled to the rate of temperature fall of 60 DEG C/min, keeps the temperature 0.3~0.5h；It is dropped again with the rate of temperature fall of 60 DEG C/min
Temperature keeps the temperature 5~10h to 1060~1080 DEG C；Finally with the cooling velocity fast cooling of 20 DEG C/min to 1000 DEG C hereinafter, obtaining
Obtain the high-strength tenacity Mo2FeB2Based ceramic metal.
The present invention additionally provides a kind of high-strength tenacity Mo simultaneously2FeB2The preparation method of based ceramic metal, including following step
It is rapid:
(1) first using Mo powder, FeB powder, Fe powder as raw material preparation mixed powder, in the mixed powder, in terms of mass parts,
Mo:48.0~51.9, Fe:42.4~46.7, B:5.3~5.7；In the composition proportion, Mo is introduced by Mo powder；Fe a part
It is introduced by FeB powder, some is introduced by Fe powder；B is introduced by FeB powder.Wherein the granularity of Mo powder is 3.5~4.0 μm, FeB
The granularity of powder is 45.0~50.0 μm, and the granularity of Fe powder is 3.0~3.5 μm；
(2) above-mentioned mixed powder feed powder is higher than 1.0 × 10 in vacuum degree after ball mill mixing, drying sieving-1The vacuum of Pa
Vacuum pre-sintering is carried out in sintering furnace, sintering temperature is 1000 DEG C, and soaking time 1h is obtained with Mo2FeB2Based on hard phase
Intermediate reaction product；
(3) intermediate reaction product that step (2) obtain is ground into intermediate reaction product powder；
(4) the smashed intermediate reaction product powder of step (3), Fe powder, Cr powder, Ni powder and graphite powder are mixed and obtains two
Secondary mixed powder, in the secondary mixed powder, in terms of mass parts, Mo:44.4~48.0, B:4.9~5.3, Fe:41.2~
44.9, Cr:2.2~2.8, Ni:2.6~3.2, C:0.1~0.4；In the composition proportion, Mo is drawn by intermediate reaction product
Enter；Fe a part is introduced by intermediate reaction product, some is introduced by Fe powder；B is introduced by intermediate reaction product；Cr is by Cr
Powder introduces；Ni is introduced by Ni powder；C is introduced by graphite powder.Wherein the granularity of intermediate reaction product powder is 1.0~5.0 μm, Fe powder
The granularity at end is 3.0~3.5 μm, and the granularity of Cr powder is 4.5~5.0 μm, and the granularity of Ni powder is 3.0~3.5 μm, the grain of graphite powder
Degree is 3.0~4.0 μm；
(5) above-mentioned mixed powder is subjected to vacuum-sintering after ball mill mixing, compression moulding in vacuum sintering furnace；It is described
Vacuum-sintering process are as follows: green compact is warming up to 1200~1240 DEG C with the heating rate of 10 DEG C/min first, is not kept the temperature；Then with
The rate of temperature fall of 60 DEG C/min is cooled to 1140~1160 DEG C, keeps the temperature 0.3~0.5h；Cooled down again with the rate of temperature fall of 60 DEG C/min
To 1060~1080 DEG C, 5~10h is kept the temperature；Finally with the cooling velocity fast cooling of 20 DEG C/min to 1000 DEG C hereinafter, obtaining
The high-strength tenacity Mo2FeB2Based ceramic metal.
Further, in the step (2), the mixing, which refers to, is in a planetary ball mill uniformly mixed mixture,
Drum's speed of rotation is 250~350rpm, and ratio of grinding media to material 5:1, Ball-milling Time is for 24 hours；
Further, it in the step (3), crushes and refers to that will be pre-sintered the intermediate reaction product obtained is placed in oscillatory type mill
It is crushed in mine machine, vibration frequency is 16.0~20.0Hz, and amplitude is 8.0~12.0mm, and grinding time is 3~5min, is obtained
Obtain intermediate reaction product powder.
Further, in the step (5), compounding process is to carry out in a planetary ball mill, drum's speed of rotation 200
~300rpm, ratio of grinding media to material 6:1, Ball-milling Time are 24~36h；
Further, in the step (5), pressure used in suppression process is 260~320MPa.
In above-mentioned technical proposal, mixture is configured using Mo powder, FeB powder, Fe powder as raw material first, and obtain by being pre-sintered
With Mo2FeB2Intermediate reaction product based on hard phase.In pre-sintered state, it can successively occur following solid phase reaction: Fe+FeB →
Fe2B；2Mo+2FeB→Mo2FeB2；2Mo+2Fe2B→Mo2FeB2+3Fe。
In above-mentioned technical proposal, step (3) is crushed to gained intermediate reaction product is pre-sintered, and makes the hard of strip
Mutually it is ground into the powder of the shaft-like such as close.Then it is mixed to get mixture with other component ingredients, so that during burning eventually, drop
Low hard phase crystal grain anisotropic growth trend, improves boride reticular structure, is conducive to filling out for eutectic liquid relative porosity factor
It fills, the consistency of final sintered body can be significantly improved.
In above-mentioned technical proposal, green compact are rapidly heated to 1200~1240 DEG C of (L by step (5) sintering stage first2Liquid
The phase sintering stage) and do not keep the temperature, it is to pass through solution modeling mechanism in undissolved coarse granule Mo2FeB2Hard phase surface shape
At one layer of Mo2(Fe,Cr)B2Complicated solid solution circular phase, and the formation of circular phase can effectively inhibit hard phase crystal grain respectively to different
Property growth.1140~1160 DEG C of (L are then cooled to the rate of temperature fall of 60 DEG C/min1The liquid-phase sintering stage) heat preservation 0.3~
0.5h, be in order to make sintered body possess relatively high consistency, due to capillarity, at this time the hole in ceramics all in
Precritical unstable state.1050~1080 DEG C (solid-phase sintering stage) heat preservations are cooled to the rate of temperature fall of 60 DEG C/min again
5~10h is to further suppress crystal grain anisotropic growth by the migration for limiting crystal boundary, and pass through to spread and complete sintering
The densification process of body.Finally make furnace temperature fast cooling to 1000 DEG C hereinafter, obtaining micro- group with the cooling velocity of 20 DEG C/min
Knit uniform, crystal grain refinement cermet.
Compared with prior art, the beneficial effects of the invention are that:
(1) the method comprises the steps of firstly, preparing with Mo2FeB2Intermediate reaction product based on hard phase can make through pulverization process
Strip hard phase becomes the shaft-like such as close, can make the whole burning stage that crystal grain anisotropic growth trend be effectively reduced, and improves boron
Change reticular structure, is conducive to the filling of eutectic liquid relative porosity factor.
(2) high-strength tenacity Mo provided by the invention2FeB2Based ceramic metal, hard phase crystal grain form core-ring structure,
Middle Mo2(Fe,Cr)B2The formation of complicated solid solution circular phase, it is suppressed that hard phase crystal grain anisotropic growth improves ceramic phase
Interface cohesion between metallic binding phase enhances the bond strength of phase interface.
(3) sintered body of the present invention is only stopped in high-temperature liquid-phase sintering stage in short-term, then long in Low Temperature Solid-Phase sintering stage
Shi Baowen completes the densification process of sintered body by diffusion, and hard phase crystal grain is obviously refined, and improves the equal of microscopic structure
Even property, has been obviously improved the comprehensive mechanical property of cermet.
(4) present invention only needs conventional equipment, is conducive to commercial introduction application.
Detailed description of the invention
Fig. 1 is high-strength tenacity Mo prepared by embodiment 12FeB2The SEM of based ceramic metal schemes.
In figure, 1, core；2, circular phase；3, Binder Phase.
Specific embodiment
Technical effect of the invention is further illustrated below in conjunction with example.
In following embodiment, vibration mill is purchased from Nanchang City Li Yuan metallurgy equipment of mining Co., Ltd, model GJ-IA type
Vibration mill；Planetary ball mill is purchased from Changsha meter Qi experimental instruments and equipment limited, the planetary ball of model YXQM-4L type
Grinding machine；Vacuum drying oven is purchased from Shanghai Chen Hua Electric Furnace Corp Ltd., model ZY-40-20Y type vacuum hotpressing stove；Compression moulding is made
Instrument is electronic powder compressing machine, is purchased from Tianjin Tianjin Keqi High Technology Corp., the electronic powder of model DY-40 type
Last tablet press machine.
Raw material used by following instance are as follows: Mo powder, FeB powder, Fe powder, Cr powder, Ni powder, graphite powder.The granularity of Mo powder
It is 3.5~4.0 μm, the granularity of FeB powder is 45.0~50.0 μm, and the granularity of Fe powder is 3.0~3.5 μm, the grain of Cr powder
Degree is 4.5~5.0 μm, and the granularity of Ni powder is that the granularity of 3.0~3.5 μm of powdered graphites is 3.0~4.0 μm.
The pre-sintering mixture of 1 four kinds of component prescriptions of table
| Ingredient | Mo | Fe | B |
| 1# | 51.9 | 42.4 | 5.7 |
| 2# | 50.2 | 44.2 | 5.6 |
| 3# | 48.9 | 45.7 | 5.4 |
| 4# | 48.0 | 46.7 | 5.3 |
The cermet mixture of 2 four kinds of component prescriptions of table
Table 1 is the pre-sintering mixed powder of 4 kinds of different component formulas, and table 2 is that the cermet of 4 kinds of different component formulas is mixed
Close powder.Each ingredient is in parts by weight in Tables 1 and 2, and 3 kinds of different technical parameters systems of embodiment 1-3 are respectively adopted
For at Mo2FeB2Based ceramic metal.The Rockwell hardness of cermet is determined using Rockwell hardness instrument；It is surveyed using universal testing machine
The bending strength of cermet is determined；Cermet is determined using microhardness testers and according to national standard GB/T4340.1-2009
Palmqvist fracture toughness.
Embodiment 1
The present embodiment cermet preparation step is as follows:
(1) using Mo powder, FeB powder, Fe powder as raw material, 4 kinds of mixed powders are prepared according to table 1；
(2) mixing: mixed powder being placed in planetary ball mill and is mixed, drum's speed of rotation 250rpm, ball material
Than for 5:1, the time is for 24 hours；
(3) it is pre-sintered: being higher than 1.0 × 10 in vacuum degree-1It is carried out in the vacuum drying oven of Pa, sintering temperature is 1000 DEG C, heat preservation
Time is 1h, is obtained with Mo2FeB2Intermediate reaction product based on hard phase；
(4) it crushes: the intermediate reaction product that step (3) obtain being placed in vibration mill and is crushed, vibration frequency
Rate is 16.0Hz, amplitude 12.0mm, grinding time 5min, obtains intermediate reaction product powder；
(5) it using intermediate reaction product obtained by step (4), Fe powder, Cr powder, Ni powder and graphite powder as raw material, is prepared according to table 2
4 kinds of mixed powders；
(6) mixing: mixed powder being placed in planetary ball mill and is mixed, drum's speed of rotation 200rpm, ball material
Than for 6:1, time 36h；
(7) compression moulding: pressure used in compression moulding is 260MPa；
Final sintering: in a vacuum furnace, green compact is warming up to 1200 DEG C with the heating rate of 10 DEG C/min first, is not protected
Temperature；1160 DEG C then are cooled to the rate of temperature fall of 60 DEG C/min, keeps the temperature 0.3h；It is cooled to again with the rate of temperature fall of 60 DEG C/min
1080 DEG C, keep the temperature 5h；Finally with the cooling velocity fast cooling of 20 DEG C/min to 1000 DEG C hereinafter, and acquisition high-strength tenacity
Mo2FeB2Based ceramic metal, SEM figure are as shown in Figure 1.As seen from Figure 1, circular phase 2 is centered around the outer of hard-phase particles core 1
It encloses, forms shaft-like hard-phase particles, the Fe base bonding phases 3 such as core-ring structure is close and be located on the outside of circular phase 2.
Performance detection is carried out to the material that the present embodiment obtains, testing result is as shown in table 3.
The performance for the different metal ceramics that 3 embodiment 1 of table is prepared
| Ingredient | 1# | 2# | 3# | 4# |
| Bending strength σb(MPa) | 2089 | 2137 | 2252 | 2348 |
| Hardness (HRA) | 88.5 | 88.1 | 87.9 | 87.6 |
| Fracture toughness (MNm-3/2) | 25.5 | 24.9 | 24.3 | 23.4 |
Embodiment 2
The present embodiment cermet preparation step is as follows:
(1) using Mo powder, FeB powder, Fe powder as raw material, 4 kinds of mixed powders are prepared according to table 1；
(2) mixing: mixed powder being placed in planetary ball mill and is mixed, drum's speed of rotation 300rpm, ball material
Than for 5:1, the time is for 24 hours；
(3) it is pre-sintered: being higher than 1.0 × 10 in vacuum degree-1It is carried out in the vacuum drying oven of Pa, sintering temperature is 1000 DEG C, heat preservation
Time is 1h, is obtained with Mo2FeB2Intermediate reaction product based on hard phase；
(4) it crushes: the intermediate reaction product that step (3) obtain being placed in vibration mill and is crushed, vibration frequency
Rate is 18.0Hz, amplitude 10.0mm, grinding time 4min, obtains intermediate reaction product powder；
(5) it using intermediate reaction product obtained by step (4), Fe powder, Cr powder, Ni powder and graphite powder as raw material, is prepared according to table 2
4 kinds of mixed powders；
(6) mixing: mixed powder being placed in planetary ball mill and is mixed, drum's speed of rotation 250rpm, ball material
Than for 6:1, time 30h；
(7) compression moulding: pressure used in compression moulding is 280MPa；
(8) final sintering: green compact is warming up to 1220 DEG C with the heating rate of 10 DEG C/min first, is not kept the temperature；Then with
The rate of temperature fall of 60 DEG C/min is cooled to 1150 DEG C, keeps the temperature 0.4h；1070 DEG C are cooled to the rate of temperature fall of 60 DEG C/min again, is protected
Warm 8h；Finally with the cooling velocity fast cooling of 20 DEG C/min to 1000 DEG C or less.
Performance detection is carried out to the material that the present embodiment obtains, testing result is as shown in table 4.
The performance for the different metal ceramics that 4 embodiment 2 of table is prepared
| Ingredient | 1# | 2# | 3# | 4# |
| Bending strength σb(MPa) | 2076 | 2101 | 2212 | 2310 |
| Hardness (HRA) | 88.6 | 88.3 | 88.1 | 87.7 |
| Fracture toughness (MNm-3/2) | 25.7 | 25.2 | 24.5 | 23.7 |
Embodiment 3
The present embodiment cermet preparation step is as follows:
(1) using Mo powder, FeB powder, Fe powder as raw material, 4 kinds of mixed powders are prepared according to table 1；
(2) mixing: mixed powder being placed in planetary ball mill and is mixed, drum's speed of rotation 350rpm, ball material
Than for 5:1, the time is for 24 hours；
(3) it is pre-sintered: being higher than 1.0 × 10 in vacuum degree-1It is carried out in the vacuum drying oven of Pa, sintering temperature is 1000 DEG C, heat preservation
Time is 1h, is obtained with Mo2FeB2Intermediate reaction product based on hard phase；
(4) it crushes: the intermediate reaction product that step (3) obtain being placed in vibration mill and is crushed, carry out powder
Broken, vibration frequency 20.0Hz, amplitude 8.0mm, grinding time 3min obtain intermediate reaction product powder；
(5) it using intermediate reaction product obtained by step (4), Fe powder, Cr powder, Ni powder and graphite powder as raw material, is prepared according to table 2
4 kinds of mixed powders；
(6) mixing: mixed powder being placed in planetary ball mill and is mixed, drum's speed of rotation 300rpm, ball material
Than for 6:1, the time is for 24 hours；
(7) compression moulding: pressure used in compression moulding is 320MPa；
(8) final sintering: green compact is warming up to 1240 DEG C with the heating rate of 10 DEG C/min first, is not kept the temperature；Then with
The rate of temperature fall of 60 DEG C/min is cooled to 1140 DEG C, keeps the temperature 0.5h；1060 DEG C are cooled to the rate of temperature fall of 60 DEG C/min again, is protected
Warm 10h；Finally with the cooling velocity fast cooling of 20 DEG C/min to 1000 DEG C or less.
Performance detection is carried out to the material that the present embodiment obtains, testing result is as shown in table 5.
The performance for the different metal ceramics that 5 embodiment 3 of table is prepared
| Ingredient | 1# | 2# | 3# | 4# |
| Bending strength σb(MPa) | 2019 | 2068 | 2184 | 2286 |
| Hardness (HRA) | 88.8 | 88.5 | 88.3 | 87.8 |
| Fracture toughness (MNm-3/2) | 26.1 | 25.4 | 24.8 | 23.9 |
In this letter of authorization value range, the technological parameter of three phases is to Effect on Mechanical Properties before second step sintering process
It is relatively large, only when the sintering temperature in this stage and reasonable soaking time collocation, the densification process ability in above-mentioned stage
It preferably completes, the cermet of above-mentioned each component prescription just can get relatively good comprehensive mechanical property.In short, in this power
In sharp book value range, above-mentioned technological factor influences the performance of cermet limited.
The above embodiments are merely intended to illustrate the present invention rather than to limit it, thus with it is of the invention
Any change in the comparable meaning and scope of claims, should be construed as being included in the scope of the claims.
There are many concrete application approach of the present invention, the above is only a preferred embodiment of the present invention, it is noted that for
For those skilled in the art, without departing from the principle of the present invention, it can also make several improvements, this
A little improve also should be regarded as protection scope of the present invention.
Claims (3)
1. a kind of high-strength tenacity Mo2FeB2Based ceramic metal, it is characterised in that: the cermet includes hard-phase particles and Fe
Base is bonded phase；
The hard-phase particles are that shaft-like particle, the core of hard-phase particles are Mo with core-ring structure is close etc.2FeB2Particle,
The circular phase of core periphery is Mo2(Fe,Cr)B2Complicated solid solution；
The Mo2FeB2The component of the mass fraction of base metal-ceramic material are as follows: Mo:44.4 ~ 48.0 part, B:4.9 ~ 5.3 part, Fe:
41.2 ~ 44.9 parts, Cr:2.2 ~ 2.8 part, Ni:2.6 ~ 3.2 part, C:0.1 ~ 0.4 part.
2. high-strength tenacity Mo as described in claim 12FeB2The preparation method of based ceramic metal, which is characterized in that including following step
It is rapid:
(1) first using Mo powder, FeB powder, Fe powder as raw material preparation mixed powder, in the mixed powder, in terms of mass parts,
Mo:48.0 ~ 51.9 part, Fe:42.4 ~ 46.7 part, B:5.3 ~ 5.7 part；Wherein the granularity of Mo powder is 3.5 ~ 4.0 μm, FeB powder
Granularity is 45.0 ~ 50.0 μm, and the granularity of Fe powder is 3.0 ~ 3.5 μm；
(2) mixed powder is higher than 1.0 × 10 in vacuum degree after ball mill mixing, drying sieving-1In the vacuum sintering furnace of Pa into
Row vacuum is pre-sintered, and sintering temperature is 1000 DEG C, and soaking time 1h obtains intermediate reaction product；
(3) intermediate reaction product for obtaining step (2), which crushes, obtains intermediate reaction product powder；
(4) intermediate reaction product powder, Fe powder, Cr powder, Ni powder and the graphite powder obtained step (3), which mixes, obtains secondary mix
Powder is closed, in the secondary mixed powder, in terms of mass parts, Mo:44.4 ~ 48.0 part, B:4.9 ~ 5.3 part, Fe:41.2 ~ 44.9
Part, Cr:2.2 ~ 2.8 part, Ni:2.6 ~ 3.2 part, C:0.1 ~ 0.4 part；In secondary mixed powder, the grain of intermediate reaction product powder
Degree is 1.0 ~ 5.0 μm, and the granularity of Fe powder is 3.0 ~ 3.5 μm, and the granularity of Cr powder is 4.5 ~ 5.0 μm, the granularity of Ni powder is 3.0 ~
3.5 μm, the granularity of graphite powder is 3.0 ~ 4.0 μm；
(5) secondary mixed powder is subjected to vacuum-sintering after ball mill mixing, compacting obtain green compact in vacuum sintering furnace；Institute
State vacuum-sintering process are as follows: green compact is warming up to 1200 ~ 1240 DEG C with the heating rate of 10 DEG C/min first, is not kept the temperature；Then
1140 ~ 1160 DEG C are cooled to the rate of temperature fall of 60 DEG C/min, keeps the temperature 0.3 ~ 0.5h；Cooled down again with the rate of temperature fall of 60 DEG C/min
To 1060 ~ 1080 DEG C, 5 ~ 10h is kept the temperature；Finally with the cooling velocity fast cooling of 20 DEG C/min to 1000 DEG C hereinafter, obtaining institute
State high-strength tenacity Mo2FeB2Based ceramic metal.
3. high-strength tenacity Mo according to claim 22FeB2The preparation method of based ceramic metal, it is characterised in that: the step
Suddenly (3) middle crushing refers to for the intermediate reaction product for being pre-sintered acquisition to be placed in vibration mill and crush, vibration frequency
For 16.0 ~ 20.0Hz, amplitude is 8.0 ~ 12.0mm, and grinding time is 3 ~ 5min, obtains intermediate reaction product powder.
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| CN115786758A (en) * | 2022-11-25 | 2023-03-14 | 西安近代化学研究所 | Mo 2 FeB 2 Preparation method of-TiN-based composite material |
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| CN114752835A (en) * | 2022-03-18 | 2022-07-15 | 南京航空航天大学 | Ti (C, N) -based metal ceramic with honeycomb structure and preparation method thereof |
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| CN115652127A (en) * | 2022-11-01 | 2023-01-31 | 西安近代化学研究所 | Near-equiaxial crystal grain Mo 2 FeB 2 Preparation method of base cermet |
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