CN108610052A - A kind of titanium diboride base complex phase ceramic and its preparation method and application - Google Patents
A kind of titanium diboride base complex phase ceramic and its preparation method and application Download PDFInfo
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Abstract
The invention belongs to complex phase ceramic technical field, a kind of titanium diboride base complex phase ceramic and its preparation method and application is disclosed.Titanium diboride (the TiB2) base complex phase ceramic is with metal Ti powder and B4C powder is raw material, and using WC balls as ball-milling medium, the ball milling mixing on high energy ball mill is made metal Ti and wraps up B4The Ti B of C4C powders, then by Ti B4C powders are made under conditions of Ar or vacuum by selective laser fusion method printing shaping.The complex phase ceramic is the ceramic material of the complicated shape with dead size.This method is directly realized by TiB2The increasing material manufacturing of base ceramics is molded, and is not necessarily to follow-up sintering or heat treatment, is effectively improved TiB2The fracture toughness of base complex phase ceramic can be applied to aerospace field as a kind of electromagnetic wave transparent material.
Description
Technical field
The invention belongs to complex phase ceramic technical fields, more particularly, to a kind of titanium diboride (TiB2) base complex phase ceramic
And its preparation method and application.
Background technology
Titanium diboride (TiB2) base complex phase ceramic material is as a kind of structural material, with excellent mechanical property, such as
The excellent properties such as high rigidity, high-strength, wear-resisting, high temperature resistant, physical and chemical stability, can be widely applied to structural member, Tool in Cutting,
Aerospace etc., but just because of its excellent mechanical property limits its processing diversification, for the pottery of complicated shape
Ceramic material is unable to get by traditional processing technology.In view of its huge application scenarios, it would be highly desirable to which exploitation is a kind of to be can be achieved to appoint
The molding of the ceramic material of meaning complicated shape.
Currently, TiB2Base complex phase ceramic moulding process has：Injection moulding, pressure filtration molding, pressure forming, is coagulated at note solidification forming
Glue casting etc..But these technologies be difficult to meet it is quick to the high-end product of personalized, fining, lightweight and complication
The demand of manufacture limits the exploitation and application of high-performance ceramic product.Although current increasing material manufacturing be applied to it is ceramic at
Type, but mainly ceramics are realized by technologies such as Stereolithography, direct extrusion forming, inkjet printing, selective laser sinterings
The increasing material manufacturing of material.For the above increases material manufacturing technology, it is required for being heat-treated in next step after shaping.Selective laser melts
Dense material can be prepared by a step, and principle is powder to be melted and molded by laser, then successively scanning superposition, printing
Go out final three-dimensional structure.However, since ceramic material usually not definite melting point or fusing point are too high (being higher than 2000 DEG C).Cause
This, there is presently no be directly molded ceramic material with selective laser fusion technology.
Based on use above background and present Research, it is direct that urgent need seeks a kind of complicated shape ceramic material of dead size
Forming method.
Invention content
In order to solve above-mentioned the shortcomings of the prior art and disadvantage, a kind of TiB is provided2Base complex phase ceramic.The complex phase is made pottery
Porcelain is the complicated shape ceramic material for having dead size.
Another object of the present invention is to provide a kind of above-mentioned TiB2The preparation method of base complex phase ceramic, this method is using choosing
Selecting property laser melting method one-step shaping prepares required shaped samples, and B is wrapped up by using metal Ti4C mixed powders were printing
It is reacted in journey, prepares complicated shape TiB2Base complex phase ceramic.
It is still another object of the present invention to provide a kind of above-mentioned TiB2The application of base complex phase ceramic.
The purpose of the present invention is realized by following technical proposals：
A kind of titanium diboride (TiB2) base complex phase ceramic, the TiB2Base complex phase ceramic is with metal Ti powder and B4C powder is original
Material, using WC balls as ball-milling medium, the ball milling mixing on high energy ball mill is made metal Ti and wraps up B4The Ti-B of C4C powders, then will
Ti-B4C powders are made under conditions of Ar or vacuum by selective laser fusion method printing shaping.
Preferably, the metal Ti powder and B4The molar ratio of C powder is (1~10)：1.
Preferably, the metal Ti powder and B4The purity of C powder is 99%, the metal Ti powder and B4The grain size of C powder is
1~100 μm.
Preferably, the time of the ball milling is 2~40h.
Preferably, the TiB2The relative density of base complex phase ceramic is more than 95%, the TiB2The hardness of base complex phase ceramic is
20~45GPa, the TiB2The fracture toughness of base complex phase ceramic is 6~12MPam1/2, the TiB2The bending resistance of base complex phase ceramic
Intensity is 500~1200MPa.
The TiB2The preparation method of base complex phase ceramic, comprises the following specific steps that：
S1. with metal Ti powder and B4C powder is that raw material is mixed using WC balls as ball-milling medium on high energy ball mill, obtains gold
Belong to Ti and wraps up B4The Ti-B of C4C powders；
S2. in the case where atmosphere is Ar or vacuum condition, by Ti-B4C powders are by laser according to the scanning of setting path, powder
Coating metal Ti, which melts, makes powder layer molding, then successively scans, final to realize selective laser fusion method printing shaping,
TiB is prepared2Base complex phase ceramic.
Preferably, the parameter of selective laser fusion method described in step S2 is：Laser intensity is 150~550J/mm3,
The laser scan rate is 200~1200mm/s, 20~200 μm of sweep span, 10~100 μm of Scan slice thickness.
It is further preferable that the parameter of selective laser fusion method described in step S2 is：Laser intensity is 400J/mm3, institute
It is 800mm/s, 100 μm of sweep span, 30 μm of Scan slice thickness to state laser scan rate.
The TiB2Base complex phase ceramic can realize the design of various complicated shapes by increases material manufacturing technology, as one kind
Electromagnetic wave transparent material has a wide range of applications in aerospace field.
Compared with prior art, the invention has the advantages that：
1. the present invention is directly realized by TiB2The increasing material manufacturing of base complex phase ceramic is molded, and is not necessarily to follow-up sintering or heat treatment；
2. the present invention realizes complicated shape TiB2The dead size of-TiC complex phase ceramics is molded；
3. the introducing of metal Ti is effectively improved TiB in the present invention2The fracture toughness of base complex phase ceramic.
Description of the drawings
Fig. 1 is powder distribution and reaction principle figure during increasing material manufacturing.
Fig. 2 is selective laser fusion method forming principle figure.
Specific implementation mode
The content further illustrated the present invention with reference to specific embodiment, but should not be construed as limiting the invention.
Unless otherwise specified, the conventional means that technological means used in embodiment is well known to those skilled in the art.Except non-specifically
Illustrate, reagent that the present invention uses, method and apparatus is the art conventional reagent, methods and apparatus.
Embodiment 1
1. with metal Ti powder (for metal Ti powder purities for 99%, grain size is 20 μm) and B4C powder (B4C powder purities are 99%, grain
10 μm of diameter) it is raw material, by Ti：B4The molar ratio of C is 4:1 proportioning is through batch mixing, using WC balls as ball-milling medium, on high energy ball mill
25h is mixed, metal Ti packages B is obtained4C mixes spherical shape Ti-B4C powders, under high-energy ball milling effect, soft metal phase Ti packages
In hard phase B4C particle surfaces, with the extension of Ball-milling Time, the energy that high-energy ball milling generates makes B4C is decomposed, and is decomposed and is generated
C and B diffuse into metal Ti, and then TiC and TiB is obtained by the reaction2Phase, as shown in Figure 1.
2. under conditions of atmosphere is Ar, metal Ti is wrapped up into B4C mixes spherical shape Ti-B4C powders are molten using selective laser
Melt method, by the scan path in Fig. 2, the first floor is that laser beam makees shuttle-scanning along X-axis (Y-axis), and gradually to Y-axis (X-axis)
Direction is moved, and after the first floor end of scan, work top declines certain distance, and laser beam continues on Y-axis (X-axis) shuttle-scanning,
And gradually moved to X-axis (Y-axis) direction, the table top that proceeds with one's work continues to decline certain altitude, and laser beam is made past along X-axis (Y-axis)
Multiple scanning, and gradually moved to Y-axis (X-axis) direction, duplicate printing always, sample is successively superimposed along forming direction, until complete
At the printing shaping of sample.Its design parameter is：Laser intensity is 400J mm3, laser scan rate 800mm/s, scanning room
Away from 100 μm, 30 μm of Scan slice thickness.Finally prepare TiB2- TiC complex phase ceramics.
Above-mentioned gained TiB2- TiC complex phase ceramics are with complex shape and dead size, the TiB2- TiC ceramics it is relatively close
Degree is 98%, hardness 35GPa, fracture toughness 12MPam1/2, bending strength 1000MPa.
Embodiment 2
With metal Ti powder (for metal Ti powder purities for 99%, grain size is 30 μm) and B4C powder (B4C powder purities are 99%, grain size
20 μm) it is raw material, according to Ti：B4The molar ratio of C is 1:1 carries out dispensing, and TiB is prepared according to 1 method of embodiment2Base ceramics, wherein
Laser intensity, sweep speed, Scan slice thickness are respectively 350J/mm3, 800mm/s and 35 μm, the atmosphere in print procedure is Ar.
The present embodiment realizes complicated shape TiB by selective laser fusion technology2-TiC-B4The dead size of C complex phase ceramics is molded, institute
State TiB2-TiC-B4The relative density of C complex phase ceramics is 98%, hardness 40GPa, fracture toughness 10MPam1/2, bending resistance is strong
Degree is 1100MPa.
Embodiment 3
With metal Ti powder (for metal Ti powder purities for 99%, grain size is 20 μm) and B4C powder (B4C powder purities are 99%, grain size
20 μm) it is raw material, according to Ti：B4The molar ratio of C is 4:1 carries out dispensing, and TiB is prepared according to 1 method of embodiment2Base ceramics, wherein
Laser intensity, sweep speed, Scan slice thickness are respectively 350J/mm3, 800mm/s and 35 μm, the atmosphere in print procedure is true
It is empty.The present embodiment realizes complicated shape TiB by selective laser fusion technology2The dead size of-TiC complex phase ceramics is molded, institute
State TiB2The relative density of-TiC complex phase ceramics is 98%, hardness 30GPa, fracture toughness 12MPam1/2, bending strength
For 1000MPa.
Embodiment 4
With metal Ti powder (for metal Ti powder purities for 99%, grain size is 40 μm) and B4C powder (B4C powder purities are 99%, grain size
40 μm) it is raw material, according to Ti：B4The molar ratio of C is 1:1 carries out dispensing, and TiB is prepared according to 1 method of embodiment2Base ceramics, wherein
Laser intensity, sweep speed, Scan slice thickness are respectively 450J/mm3, 500mm/s and 45 μm, the atmosphere in print procedure is true
It is empty.The present embodiment realizes complicated shape TiB by selective laser fusion technology2-TiC-B4The dead size of C complex phase ceramics is molded,
The TiB2-TiC-B4The relative density of C complex phase ceramics is 99%, hardness 42GPa, fracture toughness 12MPam1/2, bending resistance
Intensity is 1200MPa.
Embodiment 5
With metal Ti powder (for metal Ti powder purities for 99%, grain size is 10 μm) and B4C powder (B4C powder purities are 99%, grain size
20 μm) it is raw material, according to Ti：B4The molar ratio of C is 6:1 carries out dispensing, and TiB is prepared according to 1 method of embodiment2Base ceramics, wherein
Laser intensity, sweep speed, Scan slice thickness are respectively 300J/mm3, 500mm/s and 30 μm, the atmosphere in print procedure is true
It is empty.The present embodiment realizes complicated shape TiB by selective laser fusion technology2The dead size of-TiC complex phase ceramics is molded, institute
State TiB2The relative density of-TiC complex phase ceramics is 99%, hardness 30GPa, fracture toughness 12MPam1/2, bending strength
For 1200MPa.
The above embodiment is a preferred embodiment of the present invention, but embodiments of the present invention are not by above-described embodiment
Limitation, it is other it is any without departing from the spirit and principles of the present invention made by change, modification, substitute, combination and simplify,
Equivalent substitute mode is should be, is included within the scope of the present invention.
Claims (9)
1. a kind of titanium diboride base complex phase ceramic, which is characterized in that the titanium diboride base complex phase ceramic be with metal Ti powder and
B4C powder is raw material, and using WC balls as ball-milling medium, the ball milling mixing on high energy ball mill is made metal Ti and wraps up B4The Ti-B of C4C
Powder, then by Ti-B4C powders are made under conditions of Ar or vacuum by selective laser fusion method printing shaping.
2. titanium diboride base complex phase ceramic according to claim 1, which is characterized in that the metal Ti powder and B4C powder rubs
You are than being (1~10)：1.
3. titanium diboride base complex phase ceramic according to claim 1, which is characterized in that the metal Ti powder and B4C powder it is pure
Degree is 99%, the metal Ti powder and B4The grain size of C powder is 1~100 μm.
4. titanium diboride base complex phase ceramic according to claim 1, which is characterized in that the time of the ball milling be 2~
40h。
5. titanium diboride base complex phase ceramic according to claim 1, which is characterized in that the titanium diboride base complex phase ceramic
Relative density be more than 95%, the hardness of the titanium diboride base complex phase ceramic is 20~45GPa, the titanium diboride base complex phase
The fracture toughness of ceramics is 6~12MPam1/2, the bending strength of the titanium diboride base complex phase ceramic is 500~1200MPa.
6. according to the preparation method of claim 1-5 any one of them titanium diboride base complex phase ceramics, which is characterized in that including
Following specific steps：
S1. with metal Ti powder and B4C powder is raw material, and using WC balls as ball-milling medium, the ball milling mixing on high energy ball mill obtains gold
Belong to Ti and wraps up B4The Ti-B of C4C powders；
S2. in the case where atmosphere is Ar or vacuum condition, by Ti-B4C powders are by laser according to the scanning of setting path, Ti-B4C powder
Surface layer metal Ti, which melts, makes powder layer molding, then successively scans, final to realize the printing of selective laser fusion method
Molding, is prepared titanium diboride base complex phase ceramic.
7. the preparation method of titanium diboride base complex phase ceramic according to claim 6, which is characterized in that described in step S2
The parameter of selective laser fusion method is：Laser intensity is 150~550J/mm3, laser scan rate is 200~1200mm/s,
20~200 μm of sweep span, 10~100 μm of Scan slice thickness.
8. the preparation method of titanium diboride base complex phase ceramic according to claim 7, which is characterized in that described in step S2
The parameter of selective laser fusion method is：Laser intensity is 400J/mm3, the laser scan rate is 800mm/s, scanning room
Away from 100 μm, 30 μm of Scan slice thickness.
9. application of the claim 1-5 any one of them titanium diboride base complex phase ceramics in aerospace field.
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| PCT/CN2018/106357 WO2019218560A1 (en) | 2018-05-17 | 2018-09-19 | Titanium diboride-based multi-phase ceramic, preparation method therefor and application thereof |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109735743A (en) * | 2019-03-22 | 2019-05-10 | 上海材料研究所 | A kind of titanium alloy composite material and preparation method thereof, laser gain material are manufactured method |
| CN110282977A (en) * | 2019-06-17 | 2019-09-27 | 东北大学 | A kind of B4C/TiB2The preparation method of layered composite ceramic material |
| CN110627508A (en) * | 2019-08-28 | 2019-12-31 | 广东工业大学 | High-entropy boride-based ceramic and preparation method and application thereof |
| CN111118323A (en) * | 2020-01-07 | 2020-05-08 | 昆明理工大学 | Preparation method of metal ceramic composite powder for laser 3D printing |
| CN112521160A (en) * | 2020-12-29 | 2021-03-19 | 山东硅纳新材料科技有限公司 | B4C/h-BN high-temperature complex-phase ceramic and preparation method thereof |
| CN113880585A (en) * | 2021-10-29 | 2022-01-04 | 武汉科技大学 | Titanium boride-boron carbide composite ceramic having complex shape and method for producing same |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101704678A (en) * | 2009-11-11 | 2010-05-12 | 昆明理工大学 | Self-propagation high-temperature synthesizing preparation method of TiB2-TiC complex ceramic micropowder |
| CN101704676A (en) * | 2009-11-11 | 2010-05-12 | 昆明理工大学 | Method for synthesizing and preparing titanium diboride-titanium carbide complex-phase ceramic micropowder at room temperature |
| CN107352999A (en) * | 2017-07-21 | 2017-11-17 | 成都职业技术学院 | A kind of analog detection method of the laser sintered performance of 3D printing inorganic material powders |
| CN107805066A (en) * | 2017-11-13 | 2018-03-16 | 成都优材科技有限公司 | The processing method of bioceramic part based on selective laser sintering |
| CN107937762A (en) * | 2017-10-20 | 2018-04-20 | 上海交通大学 | In-situ self-generated TiB is prepared based on SLM2Strengthen the method for composite material |
| CN107973607A (en) * | 2016-10-21 | 2018-05-01 | 南京理工大学 | A kind of ceramic slurry selective laser fusing/thermal sintering method of binder free |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104928513B (en) * | 2015-07-09 | 2017-08-25 | 哈尔滨工业大学 | A kind of titanium alloy laser 3D printing improved method |
| CN106636841B (en) * | 2016-10-13 | 2018-01-05 | 聊城大学 | A kind of metal microporous material and preparation method thereof |
| CN107127342B (en) * | 2017-04-19 | 2020-05-19 | 华中科技大学 | Technological method for powder bed multi-material area laying forming |
| CN107130138B (en) * | 2017-05-19 | 2018-09-04 | 淮阴工学院 | The method of medical high abrasion titanium alloy composite material and 3D printing gradient in-situ nano complex phase anti-attrition medical titanium alloy |
-
2018
- 2018-05-17 CN CN201810475218.0A patent/CN108610052A/en active Pending
- 2018-09-19 WO PCT/CN2018/106357 patent/WO2019218560A1/en active Application Filing
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101704678A (en) * | 2009-11-11 | 2010-05-12 | 昆明理工大学 | Self-propagation high-temperature synthesizing preparation method of TiB2-TiC complex ceramic micropowder |
| CN101704676A (en) * | 2009-11-11 | 2010-05-12 | 昆明理工大学 | Method for synthesizing and preparing titanium diboride-titanium carbide complex-phase ceramic micropowder at room temperature |
| CN107973607A (en) * | 2016-10-21 | 2018-05-01 | 南京理工大学 | A kind of ceramic slurry selective laser fusing/thermal sintering method of binder free |
| CN107352999A (en) * | 2017-07-21 | 2017-11-17 | 成都职业技术学院 | A kind of analog detection method of the laser sintered performance of 3D printing inorganic material powders |
| CN107937762A (en) * | 2017-10-20 | 2018-04-20 | 上海交通大学 | In-situ self-generated TiB is prepared based on SLM2Strengthen the method for composite material |
| CN107805066A (en) * | 2017-11-13 | 2018-03-16 | 成都优材科技有限公司 | The processing method of bioceramic part based on selective laser sintering |
Non-Patent Citations (1)
| Title |
|---|
| 郭晓琴等: "激光熔覆反应合成 Cu-TiB2复合材料的工艺与组织研究", 《热加工工艺》 * |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109735743A (en) * | 2019-03-22 | 2019-05-10 | 上海材料研究所 | A kind of titanium alloy composite material and preparation method thereof, laser gain material are manufactured method |
| CN110282977A (en) * | 2019-06-17 | 2019-09-27 | 东北大学 | A kind of B4C/TiB2The preparation method of layered composite ceramic material |
| CN110627508A (en) * | 2019-08-28 | 2019-12-31 | 广东工业大学 | High-entropy boride-based ceramic and preparation method and application thereof |
| CN111118323A (en) * | 2020-01-07 | 2020-05-08 | 昆明理工大学 | Preparation method of metal ceramic composite powder for laser 3D printing |
| CN112521160A (en) * | 2020-12-29 | 2021-03-19 | 山东硅纳新材料科技有限公司 | B4C/h-BN high-temperature complex-phase ceramic and preparation method thereof |
| CN113880585A (en) * | 2021-10-29 | 2022-01-04 | 武汉科技大学 | Titanium boride-boron carbide composite ceramic having complex shape and method for producing same |
| CN113880585B (en) * | 2021-10-29 | 2023-10-27 | 武汉科技大学 | Titanium boride-boron carbide composite ceramic with complex shape and manufacturing method thereof |
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