CN102976755B - Laser cladding preparation process of Ti(C,N) ceramic - Google Patents
Laser cladding preparation process of Ti(C,N) ceramic Download PDFInfo
- Publication number
- CN102976755B CN102976755B CN201210444897.8A CN201210444897A CN102976755B CN 102976755 B CN102976755 B CN 102976755B CN 201210444897 A CN201210444897 A CN 201210444897A CN 102976755 B CN102976755 B CN 102976755B
- Authority
- CN
- China
- Prior art keywords
- laser
- powder
- purity
- ceramic
- preparation technology
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
Landscapes
- Compositions Of Oxide Ceramics (AREA)
- Ceramic Products (AREA)
Abstract
The invention relates to a laser cladding preparation process of Ti(C,N) ceramic. Through in-depth study of ceramic samples prepared by using laser, it is found that laser power and scan speed greatly influence material microstructures. When the two factors are adjusted, a good microstructure can be obtained. Also, single-phase metal Mo has the functions of improving metal wettability upon hard phases and inhibiting crystal grain growth. Therefore, when a proper amount of metal Mo is added into Ti(C,N), a better internal structure can be obtained. Based on the above theories, the invention provides Ti(C,N) ceramic with a good microstructure, and a preparation method of Ti(C,N) ceramic can be improved.
Description
Technical field
The invention belongs to the technical field of high temperature ceramic material, relate to the laser melting coating preparation technology of a kind of Ti (C, N) pottery.Specifically adopt batch mixing, press and to form type, then base substrate is carried out laser sintered, preparation has the material of good resistance to elevated temperatures.
Background technology
Ti (C, N) based ceramic metal is owing to having higher hardness, wear resistance, and low thermal expansivity and good chemical stability, become a kind of potential material, gets more and more people's extensive concerning.Its application in productive life mainly contains high-precision cutter die, engine, the high temperature resistant components such as jet pipe, the wear-resistant coating layer of mechanical component etc.
Ti (C, N) based ceramic metal is a kind of in aerospace, the stupalith of field of machining extensive application.In industry, the most frequently used preparation method uses High Temperature Furnaces Heating Apparatus to carry out sintering, but the common length consuming time of this method, and consume a large amount of energy.Along with going deep into of research, it is found that laser sintered more more superior than High Temperature Furnaces Heating Apparatus.Laser sinteredly can carry out three-dimensional growth, can process and prepare some irregular parts, preparation cycle also shortens greatly.But laser sintered also have a shortcoming, because molding time is very short, the sample that the microtexture of material is prepared not as High Temperature Furnaces Heating Apparatus, density is also lower slightly.Therefore with the laser sintered sample with good microtexture of preparing, there is very high practical value.
Owing to using High Temperature Furnaces Heating Apparatus to prepare the complex process of stupalith, the production cycle is long, and cost is very high, in actual production, is restricted.The mode of production that the shape of various ceramic components is tending towards complicated and high energy consumption is inefficient, traditional preparation method is more and more not suitable for ceramic preparation.
Summary of the invention
The technical problem solving
For fear of the deficiencies in the prior art part, the present invention proposes the laser melting coating preparation technology of a kind of Ti (C, N) pottery, improves ceramic preparation efficiency, and technique is comparatively simple and can greatly shorten the preparation method of preparation time.
Technical scheme
A laser melting coating preparation technology for Ti (C, N) pottery, is characterized in that step is as follows:
Step 1: TiC powder, TiN powder and metal M o powder are pressed to mole mass ratio (38 ~ 42): 5:2 evenly mixes, and grinds 1 ~ 2 hour;
Step 2: add binding agent and continue to grind about half hour, binder content is 2% of mixed powder total mass; Described Binder Composition is the paraffin PW of 75.44wt%, the ethylene-vinyl acetate copolymer EVA of 22.28wt% and the titanic acid ester TC of 2.28wt%;
Step 3: the pressure by ground mixed powder with 20 ~ 25Mpa is cold-pressed into
cylindrical base substrate, pressurize one minute, then base substrate is in baking oven dry 4 hours, drying temperature is 90 ℃;
Step 4: adopt laser beam to carry out sintering dried base substrate, laser power is respectively 300W ~ 700W; Sweep velocity is respectively 1mm/s ~ 4mm/s, and laser works stroke is 1 ~ 2cm, and spot diameter 1mm, under the protection of sintering process in high-purity Ar gas.
The purity >99% of described TiC powder, particle size <8 μ m.
Described TiN powder purity >99%, particle size <5 μ m.
Described metal M o powder purity >99.99%, particle size <5 μ m.
Described laser beam sintering adopts 1000W CW Nd:YAG high power CW solid statelaser.
Beneficial effect
Ti (C provided by the invention, N) the laser melting coating preparation technology of pottery, the further investigation of the performance by ceramics sample that laser is prepared, the power of laser and sweep velocity have a great impact the microtexture tool of material, adjust this two factors, likely obtain good microtexture.In addition, because Single Phase Metal Mo has, improve the effect of metallographic phase to the wettability of hard phase and inhibiting grain growth, therefore, in Ti (C, N), add appropriate metal M o, also likely obtain better interior tissue.Based on above theory, the present invention has prepared Ti (C, the N) pottery with good microtexture, is expected to improve the preparation method of Ti (C, N) pottery.
The laser sintered preparation cycle that can greatly shorten Ti (C, N) pottery, reduces energy consumption, reduces production cost.By adulterating or adjusting laser power and sweep velocity, likely obtain good interior tissue, obtain having the ceramics sample of superperformance.The laser sintered efficiency that can improve production, also can prepare the part that shape is comparatively complicated, is applicable to present scale operation.More diversified by laser sintered its microtexture of the ceramics sample obtaining.The performance of pottery depends on the size of crystal grain to a great extent, and the size of crystal grain is along with the increase of laser energy density presents the trend that first reduces rear increase, energy density depends on power and the sweep velocity of laser, therefore can prepare Ti (C, N) pottery according to laser power and sweep velocity.This is that ceramic being used widely in high temperature material field of Ti (C, N) provides possibility.
Accompanying drawing explanation
Fig. 1: the microtexture that is Ti (C, N) pottery under the different laser powers that obtain of the present invention
(a)P=300W；(b)P=400W；(c)P=500W；(d)P=600W；(e)P=700W；
Fig. 2: the XRD figure that is the ceramics sample that obtains of the present invention.
Embodiment
Now in conjunction with the embodiments, the invention will be further described for accompanying drawing:
Embodiment 1
1. by TiC powder (purity >99%, particle size <8 μ m) and TiN powder (purity >99%, particle size <5 μ m) and metal M o powder (purity >99.99%, particle size <5 μ m) by mole mass ratio 38:5:2, mix, and grind 1 hour to mixing.2. in mixed powder, add binding agent, Binder Composition is paraffin (PW) 75.44wt%, ethylene-vinyl acetate copolymer (EVA) 22.28wt%, titanic acid ester (TC) 2.28wt%, binder content is 2% of mixed powder total mass, continues to grind half hour.3. by ground mixed powder, the pressure with 20Mpa is cold-pressed into
cylindrical base substrate, pressurize one minute, base substrate in baking oven dry 4 hours, drying temperature is 90 ℃.4. then the base substrate being dried is placed on worktable, with laser beam (1000W CWNd:YAG high power CW solid statelaser), carries out sintering, laser power is 400W, and sweep velocity is 2mm/s.5. experiment records ceramic particle size and is about 3 μ m.
Embodiment 2
1. by TiC powder (purity >99%, particle size <8 μ m) and TiN powder (purity >99%, particle size <5 μ m) and metal M o powder (purity >99.99%, particle size <5 μ m) by mole mass ratio 40:5:2, mix, and grind 1.5 hours to mixing.2. in mixed powder, add binding agent, Binder Composition is paraffin (PW) 75.44wt%, ethylene-vinyl acetate copolymer (EVA) 22.28wt%, titanic acid ester (TC) 2.28wt%, binder content is 2% of mixed powder total mass, continues to grind half hour.3. by ground mixed powder, the pressure with 20Mpa is cold-pressed into
cylindrical base substrate, pressurize one minute, base substrate in baking oven dry 4 hours, drying temperature is 90 ℃.4. then the base substrate being dried is placed on worktable, with laser beam (1000W CWNd:YAG high power CW solid statelaser), carries out sintering, laser power is 500W, and sweep velocity is 2mm/s.5. experiment records ceramic particle size and is about 1 μ m.
Embodiment 3
1. by TiC powder (purity >99%, particle size <8 μ m) and TiN powder (purity >99%, particle size <5 μ m) and metal M o powder (purity >99.99%, particle size <5 μ m) by mole mass ratio 42:5:2, mix, and grind 2 hours to mixing.2. in mixed powder, add binding agent, Binder Composition is paraffin (PW) 75.44wt%, ethylene-vinyl acetate copolymer (EVA) 22.28wt%, titanic acid ester (TC) 2.28wt%, binder content is 2% of mixed powder total mass, continues to grind half hour.3. by ground mixed powder, the pressure with 25Mpa is cold-pressed into
cylindrical base substrate, pressurize one minute, base substrate in baking oven dry 4 hours, drying temperature is 90 ℃.4. then the base substrate being dried is placed on worktable, with laser beam (1000W CWNd:YAG high power CW solid statelaser), carries out sintering, laser power is 600W, and sweep velocity is 1mm/s.5. experiment records ceramic particle size and is about 6 μ m.
Claims (5)
1. a laser melting coating preparation technology for Ti (C, N) pottery, is characterized in that step is as follows:
Step 1: TiC powder, TiN powder and metal M o powder are pressed to mole mass ratio (38～42): 5:2 evenly mixes, and grinds 1～2 hour;
Step 2: add binding agent and continue to grind half hour, binder content is 2% of mixed powder total mass; Described Binder Composition is the paraffin PW of 75.44wt%, the ethylene-vinyl acetate copolymer EVA of 22.28wt% and the titanic acid ester TC of 2.28wt%;
Step 3: the pressure by ground mixed powder with 20～25MPa is cold-pressed into
cylindrical base substrate, pressurize one minute, then base substrate is in baking oven dry 4 hours, drying temperature is 90 ℃;
Step 4: adopt laser beam to carry out sintering dried base substrate, laser power is respectively 300W～700W; Sweep velocity is respectively 1mm/s～4mm/s, and laser works stroke is 1～2cm, and spot diameter 1mm, under the protection of sintering process in high-purity Ar gas.
2. the laser melting coating preparation technology of Ti (C, N) pottery according to claim 1, is characterized in that: the purity >99% of described TiC powder, particle size <8 μ m.
3. the laser melting coating preparation technology of Ti (C, N) pottery according to claim 1, is characterized in that: described TiN powder purity >99%, particle size <5 μ m.
4. the laser melting coating preparation technology of Ti (C, N) pottery according to claim 1, is characterized in that: described metal M o powder purity >99.99%, particle size <5 μ m.
5. the laser melting coating preparation technology of Ti (C, N) pottery according to claim 1, is characterized in that: described laser beam sintering adopts 1000W CW Nd:YAG high power CW solid statelaser.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201210444897.8A CN102976755B (en) | 2012-11-08 | 2012-11-08 | Laser cladding preparation process of Ti(C,N) ceramic |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201210444897.8A CN102976755B (en) | 2012-11-08 | 2012-11-08 | Laser cladding preparation process of Ti(C,N) ceramic |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102976755A CN102976755A (en) | 2013-03-20 |
| CN102976755B true CN102976755B (en) | 2014-04-02 |
Family
ID=47851164
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201210444897.8A Expired - Fee Related CN102976755B (en) | 2012-11-08 | 2012-11-08 | Laser cladding preparation process of Ti(C,N) ceramic |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN102976755B (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105386041B (en) * | 2015-12-10 | 2017-12-15 | 西北有色金属研究院 | A kind of method that laser melting coating prepares modified compound Hf Ta metal coatings |
| CN106929617A (en) * | 2017-05-15 | 2017-07-07 | 鞍山盛晨耐火材料有限公司 | A kind of method that laser melting coating prepares furnace retaining type blast furnace carbon brick |
| CN108840687A (en) * | 2018-07-26 | 2018-11-20 | 深圳市东川技术研究有限公司 | A kind of high-intensitive sintering process for matching grand new material |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101805903A (en) * | 2010-04-12 | 2010-08-18 | 太原理工大学 | Method for cladding copper alloy layer on surface of steel substrate by laser brazing |
| CN102277018A (en) * | 2011-07-20 | 2011-12-14 | 合肥工业大学 | High-temperature self-lubricating wear-resistant powder coating |
| CN102503158A (en) * | 2011-09-29 | 2012-06-20 | 南京工业大学 | Inorganic nanometer transparent heat insulation coated glass online manufacturing device and production technology thereof |
-
2012
- 2012-11-08 CN CN201210444897.8A patent/CN102976755B/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101805903A (en) * | 2010-04-12 | 2010-08-18 | 太原理工大学 | Method for cladding copper alloy layer on surface of steel substrate by laser brazing |
| CN102277018A (en) * | 2011-07-20 | 2011-12-14 | 合肥工业大学 | High-temperature self-lubricating wear-resistant powder coating |
| CN102503158A (en) * | 2011-09-29 | 2012-06-20 | 南京工业大学 | Inorganic nanometer transparent heat insulation coated glass online manufacturing device and production technology thereof |
Non-Patent Citations (2)
| Title |
|---|
| 激光熔覆原位生成Ti(C0.3N0.7)颗粒增强镍基复合熔覆层;齐勇田 等;《应用激光》;20080430;第28卷(第2期);第135-138页 * |
| 齐勇田 等.激光熔覆原位生成Ti(C0.3N0.7)颗粒增强镍基复合熔覆层.《应用激光》.2008,第28卷(第2期),第135-138期. |
Also Published As
| Publication number | Publication date |
|---|---|
| CN102976755A (en) | 2013-03-20 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN103113112B (en) | Preparation method of metal toughened ceramic-based composite material turbine blade | |
| CN103572087B (en) | The preparation method of boron carbide particles reinforced aluminum matrix composites | |
| CN103130508B (en) | Method for preparing texturing boride super-high-temperature ceramic | |
| CN105732050A (en) | Preparation technology of net size transparent ceramic part in complex shape | |
| CN102115332B (en) | High-strength beta-SiAlON ceramic and pressureless sintering preparation method thereof | |
| CN104150940B (en) | Silicon nitride and silicon carbide complex phase porous ceramics and preparation method thereof | |
| CN104402441B (en) | A kind of low temperature Fast Sintering is prepared the method for boron carbide ceramics material | |
| CN104529421B (en) | A kind of preparation method of thin brilliant mullite ceramic | |
| CN112250442B (en) | Preparation method of high-toughness binderless nanocrystalline hard alloy | |
| CN104045350B (en) | Method for preparing silicon nitride /silicon carbide ceramic composite by use of reaction sintering process | |
| CN104149038B (en) | Diamond wheel employing ceramic binding agent | |
| CN103613388B (en) | Method for low-temperature synthesis of TiB2-Ti ceramic composite material | |
| CN102976755B (en) | Laser cladding preparation process of Ti(C,N) ceramic | |
| CN102653470B (en) | Cr2AlC ceramic target and preparation method thereof by vacuum hot pressing | |
| CN103820691B (en) | A kind of normal pressure-sintered preparation method of FeAl/TiC matrix material | |
| CN104131208A (en) | Aluminium oxide-titanium carbide micron composite ceramic cutter material and microwave sintering method thereof | |
| Duan et al. | Effect of solid contents on the mechanical properties of SiC–10 wt.% AlN ceramic composites prepared by gelcasting | |
| CN104418608B (en) | The easy fired method of carborundum porous ceramics | |
| CN104355626A (en) | Method for preparing electric conduction Si3N4-ZrB2 complex phase ceramics at low temperature | |
| CN104402450A (en) | Method for quickly preparing Ti2AlN ceramic powder on the basis of thermal explosion reaction at low temperature | |
| CN104162661A (en) | Al2O3-TiC-TiN micron composite ceramic cutter material and microwave sintering method thereof | |
| CN104926307B (en) | A kind of Ti2The reactive spray synthesis preparation method of AlC composite ceramic materials | |
| CN105218100A (en) | A kind of low-temperature growth Ti 2the method of AlC stupalith | |
| CN102392149B (en) | Method for microwave sintering preparation of nano-metric rare earth modified steel-bonded hard alloy | |
| CN105601283A (en) | Making method for Si3N4 ceramic of conductive network structure |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20140402 Termination date: 20161108 |